Multi-terminal memtransistors, fabricating methods and applications of same

ABSTRACT

One aspect of the invention relates to a multi-terminal memtransistor. The memtransistor includes a substrate having a first surface and an opposite, second surface, a polycrystalline monolayer film formed of an atomically thin material on the first surface of the substrate, an electrode array having a plurality of electrodes spatial-apart formed on the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween, and a gate electrode formed on the second surface of the substrate and capacitively coupled with the channel. The polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof. The multi-terminal memtransistor operates much like a neuron by performing both memory and information processing, and can be a foundational circuit element for new forms of neuromorphic computing.

CROSS-REFERENCE TO RELATED PATENT APPLICATION

This application claims priority to and the benefit of U.S. provisional patent application Ser. No. 62/599,946, filed Dec. 18, 2017, entitled “MULTI-TERMINAL MEMTRANSISTORS, FABRICATING METHODS AND APPLICATIONS OF SAME,” by Vinod K. Sangwan, Hong-Sub Lee and Mark C. Hersam, which is incorporated herein in its entirety by reference.

STATEMENT AS TO RIGHTS UNDER FEDERALLY-SPONSORED RESEARCH

This invention was made with government support under DMR-1720139 and EFRI-1433510 awarded by the National Science Foundation, and under 70NANB14H012 awarded by the National Institute of Standards and Technology. The government has certain rights in the invention.

Some references, which may include patents, patent applications and various publications, are cited and discussed in the description of this invention. The citation and/or discussion of such references is provided merely to clarify the description of the present invention and is not an admission that any such reference is “prior art” to the invention described herein. All references cited and discussed in this specification are incorporated herein by reference in their entireties and to the same extent as if each reference was individually incorporated by reference. In terms of notation, hereinafter, “[n]” represents the nth reference cited in the reference list. For example, [20] represents the 20th reference cited in the reference list, namely, Sangwan, V. K. et al. Gate-tunable memristive phenomena mediated by grain boundaries in single-layer MoS₂ . Nat. Nanotechnol. 10, 403-406 (2015).

FIELD OF THE INVENTION

The present invention relates generally to the field of neuromorphic computing, and more particularly to multi-terminal memtransistors using a polycrystalline monolayer film of an atomically thin material containing grains defining a plurality of grain boundaries thereof, fabricating methods and applications of the same.

BACKGROUND OF THE INVENTION

The background description provided herein is for the purpose of generally presenting the context of the invention. The subject matter discussed in the background of the invention section should not be assumed to be prior art merely as a result of its mention in the background of the invention section. Similarly, a problem mentioned in the background of the invention section or associated with the subject matter of the background of the invention section should not be assumed to have been previously recognized in the prior art. The subject matter in the background of the invention section merely represents different approaches, which in and of themselves may also be inventions. Work of the presently named inventors, to the extent it is described in the background of the invention section, as well as aspects of the description that may not otherwise qualify as prior art at the time of filing, are neither expressly nor impliedly admitted as prior art against the invention.

In the last decade, a 2-terminal passive circuit element called a memristor has been developed for non-volatile resistive random access memory and has more recently shown promise for neuromorphic computing [1-6]. Compared to flash memory, memristors have higher endurance, multi-bit data storage, and faster read/write times [4, 7, 8]. However, although 2-terminal memristors have demonstrated basic neural functions, synapses in the human brain outnumber neurons by more than a factor of 1000, which implies that multi-terminal memristors are needed to perform complex functions such as heterosynaptic plasticity [3, 9-13]. Previous attempts to move beyond 2-terminal memristors include the 3-terminal Widrow-Hoff memistor [14] and field-effect transistors with nanoionic gates [15] or floating gates [16], albeit without memristive switching in the transistor [17].

Therefore, a heretofore unaddressed need exists in the art to address the aforementioned deficiencies and inadequacies.

SUMMARY OF THE INVENTION

One of the objectives of this invention is to provide circuitries and devices capable of neuromorphic computing, and in particular a scalable realization of a multi-terminal hybrid memristor and transistor (i.e., memtransistor) using a polycrystalline monolayer film of an atomically thin material, such as MoS₂ for example.

In one aspect, the invention relates to a memtransistor. In certain embodiments, the memtransistor includes a substrate having a first surface and an opposite, second surface; a polycrystalline monolayer film formed of an atomically thin material on the first surface of the substrate; an electrode array having a plurality of electrodes spatial-apart formed on the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween; and a gate electrode formed on the second surface of the substrate and capacitively coupled with the channel. The polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof. In certain embodiments, the grains have an average grain size of about 1-10 μm.

In certain embodiments, the atomically thin material comprises MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials.

In one embodiment, the substrate is formed of oxidized silicon (SiO₂), or dielectrics including alumina, hafnia, or zirconia.

In certain embodiments, the gate electrode is formed of highly doped silicon (Si), or other conductive materials.

In certain embodiments, each electrode of the electrode array is formed of a same metallic material or different metallic materials. In one embodiment, the electrode array is formed of at least one of gold (Au), titanium (Ti), and other conductive materials.

In certain embodiments, the memtransistor is configured such that the Schottky barrier localized at each electrode is dynamically tunable so as to cause switching from a high resistance state (HRS) to a low resistance state (LRS) or from the LRS to the HRS in the memtransistor. In certain embodiments, the memtransistor is an LRS-HRS memtransistor or an LRS-LRS memtransistor.

In certain embodiments, the memtransistor combines resistive switching with transistor gating to realize nonlinear charge transport with wide tunability of individual states and switching ratios.

In certain embodiments, a switching mechanism of the memtransistor is characterizable with two memristors at the contacts connected by a field-effect transistor.

In certain embodiments, the grain boundaries in the polycrystalline monolayer film enable the memtransistor to have large switching ratios and prevent electrical breakdown by lowering the Schottky barriers through dynamic defect migration, and control devices on single grains of the polycrystalline monolayer film show a qualitatively different reversible breakdown phenomenon.

In certain embodiments, the memtransistor is fabricated in a field-effect geometry with channel lengths (L) and widths (W), each varying from 1 μm to 250 μm. In one embodiment, L=1-15 μm, and W=100-150 μm.

In another aspect, the invention relates to a memtransistor. In certain embodiments, the memtransistor includes a polycrystalline monolayer film formed of an atomically thin material, where the polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof; and an electrode array formed on the polycrystalline monolayer film, wherein the electrode array has a plurality of electrodes electrically coupled with the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween. In certain embodiments, the grains have an average grain size of about 1-10 μm.

In certain embodiments, the atomically thin material comprises MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials.

In certain embodiments, each electrode of the electrode array is formed of a same metallic material or different metallic materials. In certain embodiments, the electrode array is formed of at least one of Au, Ti, and other conductive materials.

In certain embodiments, the memtransistor further includes a gate electrode capacitively coupled with the channel.

In certain embodiments, the gate electrode is formed of highly doped Si, or other conductive materials.

In certain embodiments, the memtransistor further has a dielectric layer formed between the polycrystalline monolayer film and the gate electrode. In certain embodiments, the dielectric layer is formed of SiO₂ or dielectrics including alumina, hafnia, or zirconia.

In certain embodiments, the memtransistor is configured such that the Schottky barrier localized at each electrode is dynamically tunable so as to cause switching from an HRS to an LRS or from the LRS to the HRS in the memtransistor.

In certain embodiments, the memtransistor combines resistive switching with transistor gating to realize nonlinear charge transport with wide tunability of individual states and switching ratios.

In certain embodiments, a switching mechanism of the memtransistor is characterizable with two memristors at the contacts connected by a field-effect transistor.

In certain embodiments, the grain boundaries in the polycrystalline monolayer film enable the memtransistor to have large switching ratios and prevent electrical breakdown by lowering the Schottky barriers through dynamic defect migration, and control devices on single grains of the polycrystalline monolayer film show a qualitatively different reversible breakdown phenomenon.

In yet another aspect, the invention relates to a circuitry has one or more memtransistors as disclosed above.

In one aspect, the invention relates to an electronic device has one or more memtransistors as disclosed above.

In another aspect, the invention relates to a method for fabricating a memtransistor. In certain embodiments, the method includes growing a polycrystalline monolayer film on a substrate, wherein the polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof; and forming an electrode array on the grown polycrystalline monolayer film, wherein the electrode array has a plurality of electrodes electrically coupled with the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween.

In certain embodiments, the polycrystalline monolayer film is grown by chemical vapor deposition (CVD) on the substrates. In certain embodiments, the polycrystalline monolayer film comprises an atomically thin material of MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials. In certain embodiments, the substrate is formed of SiO₂, or dielectrics including alumina, hafnia, or zirconia.

In certain embodiments, the method further includes, prior to forming the electrode array on the grown polycrystalline monolayer film, coating a film of photoresist on the polycrystalline monolayer film to form a first structure; baking the first structure; exposing the first structure to UV light and developing the exposed first structure to form a second structure; patterning the second structure with a resist mask by reactive ion etching to form a third structure; and submerging the third structure in an N-Methyl-2-pyrrolidone (NMP) bath to remove the resist mask to form a patterned polycrystalline monolayer strips. In certain embodiments, the memtransistor is an LRS-LRS memtransistors.

In certain embodiments, the method further includes, prior to coating the film of photoresist on the polycrystalline monolayer film, coating a film of polymethylglutarimide (PMGI) on the polycrystalline monolayer film; and baking the coated film of polymethylglutarimide (PMGI) on the polycrystalline monolayer film at about 170° C. for a period of time. In certain embodiments, the memtransistor is an LRS-HRS memtransistor.

In certain embodiments, the electrode array is formed by patterning a negative photoresist, followed by thermal evaporation of metals and lift-off in NMP.

In certain embodiments, the method further includes forming a gate electrode on the substrate such that the substrate is positioned between the gate electrode and the polycrystalline monolayer film, wherein the gate electrode is capacitively coupled with the channel. In certain embodiments, the gate electrode is formed of highly doped Si, or other conductive materials.

These and other aspects of the present invention will become apparent from the following description of the preferred embodiment taken in conjunction with the following drawings, although variations and modifications therein may be affected without departing from the spirit and scope of the novel concepts of the disclosure.

BRIEF DESCRIPTION OF THE DRAWINGS

The accompanying drawings illustrate one or more embodiments of the invention and together with the written description, serve to explain the principles of the invention. Wherever possible, the same reference numbers are used throughout the drawings to refer to the same or like elements of an embodiment.

FIGS. 1A-1G show architecture of the MoS₂ memtransistor according to embodiments of the invention. FIG. 1A shows optical micrograph of CVD-grown polycrystalline monolayer molybdenum disulfide (MoS₂). The darker regions are from sparse regions of bilayer MoS₂. FIG. 1B shows spatial mapping of photoluminescence intensity (wavelength=670 nm) for the area shown in FIG. 1A. The darkest regions correspond to bilayer MoS₂, while the additional features correspond to grain boundaries within monolayer MoS₂. FIG. 1C shows lateral force microscopy retrace image of monolayer MoS₂ showing grain boundaries (see FIG. 5E for topography image). FIG. 1D shows optical micrograph of an array of MoS₂ monolayer strips with varying width (W), etched by reactive ion etching (RIE) before metallization. FIG. 1E shows optical micrograph of fully fabricated MoS₂ memtransistors with varying channel length (L). FIG. 1F shows schematic of the MoS₂ memtransistor device on 300 nm thick thermal SiO₂ on doped Si (gate). FIG. 1G shows schematic of a memtransistor device.

FIGS. 2A-2F show charge transport characteristics, endurance, retention, and statistics of MoS₂ memtransistors according to embodiments of the invention. FIG. 2A shows I-V characteristics (open circles) of a MoS₂ memtransistor (L=5 μm, W=100 μm) at a gate bias V_(G)=10 V. The direction of the drain bias (V_(D)) sweep 1→4 is highlighted with colored arrows. The sweep rate is 10 V/s throughout unless mentioned otherwise. The solid green line is simulated data from a memtransistor model (see FIGS. 11A-11E). FIG. 2B shows I-V characteristics showing 10 consecutive sweeps at each gate bias V_(G) for the same device where the switching directions are shown by the curved arrows. V_(G) was stepped down between each V_(D) sweep cycle. FIG. 2C shows transfer characteristics of a memtransistor at V_(D)=0.1 V showing a shift in threshold voltage (V_(th)) and field-effect mobility (μ) from V_(th)=20 V and μ being about 0.6 cm²/Vs in a high resistance state (HRS) to V_(th)=10 V and μ being about 0.3 cm²/Vs in a low resistance state (LRS). The curves cross at V_(G)=V_(cross) about 30 V. FIG. 2D shows endurance of current (top) and on/off ratio (bottom) characteristics at V_(D)=0.5 V in HRS (sweep 1) and LRS (sweep 2) states for 475 consecutive sweep cycles of a memristor at V_(G)=40 V (see FIGS. 7D-7K for all I_(D)-V_(D) curves). FIG. 2E shows retention of HRS and LRS currents measured at V_(D)=100 mV and V_(G)=0 V for 24 hours. The inset shows the gate-tunability of the switching ratio. FIG. 2F shows histogram of the largest on/off ratio of 62 distinct memtransistors (L=5 μm, W=100 μm), where the distribution is fit with a log-normal curve with mean and variance in log(I_(LRS)/I_(HRS)) of 1.96 and 0.54, respectively.

FIGS. 3A-3E show in situ measurements and switching mechanism according to embodiments of the invention. FIG. 3A shows EFM phase image of a MoS₂ memtransistor at V_(D)=5 V, V_(S)=0 V, and V_(tip)=0 V in forward HRS. FIG. 3B shows line profiles of EFM phase along the red dashed lines in FIG. 3A for EFM images taken at forward HRS, forward LRS, reverse HRS, and reverse LRS, respectively, as shown schematically on the right (see FIGS. 9C-9F for EFM images). Dashed ovals show band-bending near the source electrode in forward HRS and LRS and near the drain in reverse LRS and HRS. The dip near the drain in the top panel is a topography artifact. FIG. 3C shows V_(G)-dependent effective Schottky barrier height (Φ_(b)) extracted from variable temperature conductivity measurements in HRS (top) and LRS (bottom). V_(FB) is a value of V_(G) where Φ_(b) deviates from the linear dependence of the thermionic emission model. The inset shows the flat band condition at V_(G)=V_(FB)=2 V, Φ_(b)=125 meV in HRS and V_(FB)=−8 V, Φ_(b)=80 meV in LRS (see FIGS. 10A-10D for details). FIG. 3D shows I-V characteristics of a LRS-LRS MoS₂ memtransistor with an about 1.5 nm thick photoresist layer under the metal contact at different V_(G). The direction of the V_(D) sweep 1→4 is highlighted by arrows. V_(G) was stepped down between each V_(D) sweep cycle. FIG. 3E shows schematic showing the energy band diagram of a LRS-LRS memtransistor at the 4 stages of switching shown in the center. E_(fp) and E_(fn) are non-equilibrium quasi-Fermi levels for holes and electrons, respectively (see FIGS. 12A-12E for details).

FIGS. 4A-4D show control devices and neural functions of memtransistors according to embodiments of the invention. FIG. 4A shows I-V characteristics (at V_(G)=60 V) of a control device on an individual monolayer MoS₂ domain without grain boundaries showing breakdown. The breakdown voltage (V_(br)) and breakdown current (I_(br)) are defined by the point preceding the sharp downward transition in sweep 1. The upper inset shows an AFM phase image of a device with degraded material near the source electrode (arrow). The lower inset shows a linear relation between I_(br) and the width of source contact W_(s) for 9 devices with different flake shapes (see FIGS. 13A-13J). FIG. 4B shows I₂₄-V₂₄ characteristics between terminal 2 and 4 of a 6-terminal MoS₂ memtransistor (left inset) at three stages of pulses at constant V_(G)=20 V: (1) black: before any pulse; (2) green: after applying four pulses of −80 V between terminals 5 and 6 while terminals 1-4 were floating; (3) red: after applying three pulses of −80 V between terminals 6 (drain) and 5 (ground) while terminals 1-4 were floating. The white dashed lines in the left inset show the edges of the patterned MoS₂. The right inset shows heterosynaptic plasticity by about 10-fold reversible changes in conductance (G=I_(ij)/V_(ij)) between all six combinations of four terminals, ij=12, 13, 14, 23, 24, and 34 (see FIGS. 14A-14H). FIG. 4C shows post-synaptic current (PSC) versus pulse number showing long-term potentiation and depression with 30 V and −30 V pulses, respectively. The solid lines show biexponential fits. FIG. 4D shows measured change in synaptic weight change (normalized to maximum weight) with relative time intervals between paired pulses of 40 V and −40 V. The solid lines are exponential fits with time constants of 1.6 and 5.5 msec for positive and negative pulses, respectively. The inset shows the timing scheme for indirect STDP. V_(G)=0 V throughout all measurements in FIGS. 4C and 4D.

FIGS. 5S-5F show materials characterization of the MoS₂ film according to embodiments of the invention. FIG. 5A shows Raman spectrum of CVD-grown polycrystalline monolayer MoS₂ using an excitation wavelength of 532 nm. Lorentzian peak fits correspond to E¹ _(2g) and A_(1g) modes. FIG. 5B shows photoluminescence spectrum of MoS₂ collected in the same microscope. FIGS. 5C-5D show XPS spectra of MoS₂ on a SiO₂/Si substrate showing Mo 3d, S 2s, and S 2p peaks. FIG. 5E shows AFM topography image corresponding to the lateral force microscopy image in FIG. 1C. FIG. 5F shows AFM topography image of the edge a MoS₂ flake showing a monolayer step height of about 0.73 nm.

FIGS. 6A-6D show AFM analysis of a residue-free photolithography process according to embodiments of the invention. FIG. 6A shows AFM topography image of the MoS₂ crystals patterned by PMGI-assisted photolithography. The dashed green line shows the location of the edge of the patterned photoresist in the left region and the white dashed line shows the triangular MoS₂ crystal domain before reactive-ion etching (RIE) etching. FIG. 6B shows zoomed-in AFM topography image from the black dashed region in FIG. 6A showing checkerboard regions of protected (1) MoS₂, (2) etched MoS₂, (3) protected SiO₂, and (4) etched SiO₂. FIG. 6C shows height profiles taken along two horizontal lines in FIG. 6B showing minimal residue left on the protected SiO₂ region. FIG. 6D shows height profiles taken along two vertical lines in FIG. 6B showing minor etching of SiO₂ under the etched MoS₂ region (2). The noise in the height profiles is due to surface roughness and tip artifacts.

FIGS. 7A-7K show leakage, dependence on bias range, bipolar resistive switching, and endurance characteristics according to embodiments of the invention. FIG. 7A shows leakage current I_(G)-V_(G) characteristics of the MoS₂ memtransistor from FIG. 2A after a high bias V_(D) sweep from 80 V to −80 V. Note that current level of 100 pA is close to instrumentation noise floor. FIG. 7B shows I_(D)-V_(D) characteristics of a memtransistor (L=15 μm, W=150 μm) for different V_(D) sweep ranges from |20| to |80| V showing increasing switching ratio with sweep range (ratio >10³ for |80| V range). FIG. 7C shows zoomed-in view of 50 sweep cycles of the device from FIG. 2B, showing an insulating state at a range of negative V_(D) values that is dependent on V_(G) and non-zero crossing suggesting memcapacitance from contacts. FIG. 7D shows I_(D)-V_(D) characteristics of a MoS₂ memtransistor during 10 consecutive unipolar positive bias sweeps of V_(D)=0 V to 80 V. FIG. 7E shows I_(D)-V_(D) characteristics of the same MoS₂ memtransistor during 10 consecutive unipolar negative bias sweeps of V_(D)=0 V to −80 V. FIG. 7F shows LRS to HRS switching of the MoS₂ memtransistor from FIG. 2B in forward bias for V_(G)>V_(cross) where V_(cross) about 35 V. FIGS. 7G-7K show I_(D)-V_(D) characteristics of the device from FIG. 2D during 475 voltage sweeps: sweeps 1-100; sweeps 100-200; sweeps 200-300; sweeps 300-400; and sweeps 400-475, respectively.

FIGS. 8A-8E show current decay in endurance characteristics according to embodiments of the invention. FIG. 8A shows exponential and stretched exponential fits to a typical subset of endurance points from FIG. 2D. The stretched exponential function is defined as I_(D)˜A−B.e^(c(n) ⁰ ^(−n)) ^(γ) I_(D)˜A−B.e^(c(n) ⁰ ^(−n)) ^(γ) , where A, B, C, and n₀ are constants and the parameter γ≈0.8. Both the exponential and stretched exponential fits show R² being about 0.97, but the stretched exponential shows a better fit at the tail end. FIG. 8B shows endurance characteristics of a memtransistor showing only one exponential decay in reverse bias (V_(D)=−10 V). FIG. 8C shows I_(D)-V_(D) characteristic (V_(G)=0 V) of a device with L=20 μm and W=150 μm showing negligible memristive loop (10 sweep cycles). FIG. 8D shows I_(D)-V_(D) characteristic (V_(G)=60 V) of a device with L=10 μm and W=5 μm showing negligible memristive loop (19 sweep cycles). FIG. 8E shows HRS and LRS retention characteristics from FIG. 2E plotted and extrapolated in log-log scale. Relaxation of the two states is currently faster than conventional filament-based memristors such as TiO₂.

FIGS. 9A-9O show in-situ electrostatic force microscopy (EFM) of a MoS₂ memtransistor according to embodiments of the invention. FIG. 9A shows schematic of the in situ EFM measurements of MoS₂ memtransistors. FIG. 9B shows AFM topography image of the device from FIG. 3A showing grain boundaries highlighted by red arrows. FIG. 9C shows reproduction of the EFM phase images from FIG. 3A in forward HRS. The phase signal profiles along the red dashed lines numbered from 1 to 10 from top to bottom are shown in FIGS. 11A-11E. FIGS. 9D-9F show EFM phase images in forward LRS, reverse LRS, and reverse HRS, respectively, that are used for line profiles shown in FIG. 3B. FIG. 9G-9O show EFM phase profiles along the red dashed lines 1-8 and 10 in FIGS. 9C-9D. EFM phase profile along line 9 is shown in FIG. 3B. All profiles are averaged over 128 lines and are normalized with the EFM phase values at the drain and source.

FIGS. 10A-10D show low temperature transport measurements of a MoS₂ memtransistor according to embodiments of the invention. FIG. 10A shows I_(D)-V_(G) characteristics of the device from FIG. 3C (in LRS) at V_(D)=0.1 V for temperature (T) varying from 300 K to 75 K at a step of 25 K. FIG. 10B shows plot of ln(I_(D)/T^(3/2)) versus 1000/T for different V_(G) to extract Schottky barrier height using the thermionic emission model [5,6]. FIGS. 10C-10D show I_(D)-V_(G) and field-effect mobility versus V_(G) of the same device in LRS and HRS, respectively. V_(th) shifts by 15 V between HRS and LRS and V_(cross) about 42 V are seen by crossing curves in FIG. 10C.

FIGS. 11A-11E show memtransistor modeling according to embodiments of the invention. FIG. 11A shows schematic of the increased doping region near the contact resulting in larger field and reduced metal-semiconductor Schottky barrier height. FIG. 11B shows simulated variation of n₁.w_(s) at the source contact for forward bias (sweep 1 and 2 from FIG. 2A). FIG. 11C shows simulation variation of n₁.w_(d) at the drain contact for reverse bias (sweep 3 and 4 from FIG. 2A). FIG. 11D shows simulated I_(D)-V_(D) characteristics of a MoS₂ memtransistor in forward bias with different V_(G) values in the range of 10 to −30 V. FIG. 11E shows simulated variation in n₁.w_(s) for the same V_(G) values. The legend between FIG. 11D and FIG. 11E applies to both plots.

FIGS. 12A-12E show LRS-LRS MoS₂ memtransistor characteristics and mechanism according to embodiments of the invention. FIG. 12A shows schematic of a LRS-LRS memtransistor where a thin photoresist layer acts as a tunnel barrier between the metal contacts and the MoS₂ film. FIG. 12B shows AFM topography images showing the step height of the photoresist left on a blank Si substrate from a process without using PMGI. Inset shows the height profile taken along the white dashed line revealing a thickness of about 1.5 nm. FIG. 12C shows gate-tunable I-V characteristics from FIG. 3D shown in the linear scale. FIG. 12D shows I_(D)-V_(D) characteristics of 50 sweep cycles of a LRS-LRS memristor from FIG. 3D. FIG. 12E is a table showing resistive switching at the source and drain contacts in LRS-HRS and LRS-LRS memtransistors during four stages of a full sweep cycle. Conditions of relative resistance values necessary for the two different switching behaviors are listed in the top right corner. Three kinds of resistive switching events A, B, and C are shown by colored arrows.

FIGS. 13A-13J show electromigration-induced degradation in control MoS₂ devices and memtransistors according to embodiments of the invention. FIG. 13A shows AFM topography images (corresponding to FIG. 4A upper inset) showing electromigration-induced degraded material (cyan arrow) near the source electrode (top). The color scale is adjusted to reveal height contrast. FIG. 13B shows AFM phase image of a device with hourglass-shaped channel (i.e., varying channel length L from 5 μm to 1 μm), showing dendritic feature along the entire source electrode (top). Without Schottky contacts, we expect a thermal hot-spot in the region of highest electric field (V_(D)/L) (i.e., only in the narrowest region in the center). Absence of such localized breakdown rules out Joule heating and favors electromigration near the source contact as the dominant phenomenon. Width of the source electrode edge (W_(s)) is shown by the white arrows. FIG. 13C shows I_(D)-V_(D) characteristics (85 sweep cycles) of a degraded polycrystalline monolayer MoS₂ memtransistor at V_(G)=0 V (L=5 μm, W=100 μm). FIG. 13D shows AFM topography image of the device from FIG. 13C showing the dendritic features enclosed by a white dashed line near the source electrode. FIG. 13E shows a series of five snapshots (left to right) from a video captured by a black and white camera during sweep ‘3’, as highlighted by the dashed red line in FIG. 13C. The red outline and dashed black line in the first frame show the probe tip and electrode pads, respectively. The middle three frames show bright spots from the light emission appearing in the channel close to the source electrode (right), as highlighted by black arrows. Light emission was observed during all 85 sweep cycles shown in FIG. 13C. FIG. 13F shows breakdown current (I_(br), defined in FIG. 4a ) showing linear correlation W_(s) for 9 single-flake control MoS₂ devices. FIG. 13G shows breakdown voltage (V_(br), defined in FIG. 4A) showing linear correlation with L, which suggests that most of the potential is dropped across the Schottky contacts. FIG. 13H shows power (I_(br)×V_(br)) showing linear correlation with channel area (L×W). FIG. 13H shows V_(br) showing no correlation with W_(s). FIG. 13J shows I_(br) also shows no correlation with L.

FIGS. 14A-14H show I-V characteristics, gate tunability and mechanism of multi-terminal heterosynaptic device according to embodiments of the invention. FIGS. 14A-14E shows low bias characteristics of 5 permutations of inner electrodes 1-4 in FIG. 4B at V_(G)=20 V, where ij=12, 13, 14, 23, 34, respectively. I₂₄-V₂₄ is shown in FIG. 4B. The legend in FIG. 14A applies to all FIGS. 14A-14E. The black curves are measured before any pulsing. The green curves were measured after applying a −80 V pulse at V₅₆ (5-drain, 6-source) four times at a voltage ramp rate of 10 V/s. The red curves were measured after applying a −80 V pulse at V₆₅ (6-drain, 5-course) three times at the same ramp rate. The conductance returns to the pre-pulse state in all combinations of electrodes. I₃₄-V₃₄ could not be measured after the V₆₅ pulse cycle. FIG. 14F shows change in conductance between 2-4 (G₂₄) with pulses V₅₆ and V₆₅ pulses for different V_(G) showing gate-tunability of heterosynaptic plasticity. FIGS. 14G-14H show spatial profile of the MoS₂ conductance band minimum (E_(c)) along two dashed lines (FIG. 14G) passing through (x) and outside (y) the side electrodes.

DETAILED DESCRIPTION OF THE INVENTION

The present invention will now be described more fully hereinafter with reference to the accompanying drawings, in which exemplary embodiments of the present invention are shown. The present invention may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the scope of the invention to those skilled in the art Like reference numerals refer to like elements throughout.

The terms used in this specification generally have their ordinary meanings in the art, within the context of the invention, and in the specific context where each term is used. Certain terms that are used to describe the invention are discussed below, or elsewhere in the specification, to provide additional guidance to the practitioner regarding the description of the invention. For convenience, certain terms may be highlighted, for example using italics and/or quotation marks. The use of highlighting and/or capital letters has no influence on the scope and meaning of a term; the scope and meaning of a term are the same, in the same context, whether or not it is highlighted and/or in capital letters. It will be appreciated that the same thing can be said in more than one way. Consequently, alternative language and synonyms may be used for any one or more of the terms discussed herein, nor is any special significance to be placed upon whether or not a term is elaborated or discussed herein. Synonyms for certain terms are provided. A recital of one or more synonyms does not exclude the use of other synonyms. The use of examples anywhere in this specification, including examples of any terms discussed herein, is illustrative only and in no way limits the scope and meaning of the invention or of any exemplified term. Likewise, the invention is not limited to various embodiments given in this specification.

It will be understood that, although the terms first, second, third, etc. may be used herein to describe various elements, components, regions, layers and/or sections, these elements, components, regions, layers and/or sections should not be limited by these terms. These terms are only used to distinguish one element, component, region, layer or section from another element, component, region, layer or section. Thus, a first element, component, region, layer or section discussed below can be termed a second element, component, region, layer or section without departing from the teachings of the present invention.

It will be understood that, as used in the description herein and throughout the claims that follow, the meaning of “a”, “an”, and “the” includes plural reference unless the context clearly dictates otherwise. Also, it will be understood that when an element is referred to as being “on,” “attached” to, “connected” to, “coupled” with, “contacting,” etc., another element, it can be directly on, attached to, connected to, coupled with or contacting the other element or intervening elements may also be present. In contrast, when an element is referred to as being, for example, “directly on,” “directly attached” to, “directly connected” to, “directly coupled” with or “directly contacting” another element, there are no intervening elements present. It will also be appreciated by those of skill in the art that references to a structure or feature that is disposed “adjacent” to another feature may have portions that overlap or underlie the adjacent feature.

It will be further understood that the terms “comprises” and/or “comprising,” or “includes” and/or “including” or “has” and/or “having” when used in this specification specify the presence of stated features, regions, integers, steps, operations, elements, and/or components, but do not preclude the presence or addition of one or more other features, regions, integers, steps, operations, elements, components, and/or groups thereof.

Furthermore, relative terms, such as “lower” or “bottom” and “upper” or “top,” may be used herein to describe one element's relationship to another element as illustrated in the figures. It will be understood that relative terms are intended to encompass different orientations of the device in addition to the orientation shown in the figures. For example, if the device in one of the figures is turned over, elements described as being on the “lower” side of other elements would then be oriented on the “upper” sides of the other elements. The exemplary term “lower” can, therefore, encompass both an orientation of lower and upper, depending on the particular orientation of the figure. Similarly, if the device in one of the figures is turned over, elements described as “below” or “beneath” other elements would then be oriented “above” the other elements. The exemplary terms “below” or “beneath” can, therefore, encompass both an orientation of above and below.

Unless otherwise defined, all terms (including technical and scientific terms) used herein have the same meaning as commonly understood by one of ordinary skill in the art to which the present invention belongs. It will be further understood that terms, such as those defined in commonly used dictionaries, should be interpreted as having a meaning that is consistent with their meaning in the context of the relevant art and the present disclosure, and will not be interpreted in an idealized or overly formal sense unless expressly so defined herein.

As used in this disclosure, “around”, “about”, “approximately” or “substantially” shall generally mean within 20 percent, preferably within 10 percent, and more preferably within 5 percent of a given value or range. Numerical quantities given herein are approximate, meaning that the term “around”, “about”, “approximately” or “substantially” can be inferred if not expressly stated.

As used in this disclosure, the phrase “at least one of A, B, and C” should be construed to mean a logical (A or B or C), using a non-exclusive logical OR. As used herein, the term “and/or” includes any and all combinations of one or more of the associated listed items.

The description below is merely illustrative in nature and is in no way intended to limit the invention, its application, or uses. The broad teachings of the invention can be implemented in a variety of forms. Therefore, while this invention includes particular examples, the true scope of the invention should not be so limited since other modifications will become apparent upon a study of the drawings, the specification, and the following claims. For purposes of clarity, the same reference numbers will be used in the drawings to identify similar elements. It should be understood that one or more steps within a method may be executed in different order (or concurrently) without altering the principles of the invention.

Computer algorithms might be performing brain-like functions, such as facial recognition and language translation, but the computers themselves have yet to operate like brains. Computers have separate processing and memory storage units, whereas the brain uses neurons to perform both functions. Neural networks can achieve complicated computation with significantly lower energy consumption compared to a digital computer. In recent years, researchers have searched for ways to make computers more neuromorphic, or brain-like, in order to perform increasingly complicated tasks with high efficiency. The field of neuromorphic computing is emerging as a leading candidate for next-generation integrated circuit technology. Historically, progress in this field has been enabled by aggressive scaling in silicon transistor technology and corresponding algorithm optimization. However, memristors better mimic the function of biological neurons than conventional silicon transistors due to physically similar ion-mediated switching. Despite this advantage, the memristor geometry is limited to two electrodes, whereas multiple connections (synapses) between individual devices (neurons) are desired for parallel computing.

This invention discloses, among other things, a multi-terminal memtransistor that combines the desirable attributes of transistors and memristors in one device, and provides a direct pathway to increasing the number of connections. The switching is achieved by defect migration in a polycrystalline monolayer film of atomically thin material (e.g., MoS₂) near the electrical contacts, as verified by physical modeling. Technologically relevant device metrics such as endurance, retention, and large-area scaling are demonstrated. Furthermore, the neuromorphic function of heterosynaptic plasticity is demonstrated in a multi-electrode memtransistor. Overall, this device concept is expected to serve as a foundational circuit element of brain-inspired computing.

In one aspect of the invention, as shown in FIGS. 1A-1G and particularly in FIGS. 1F-1G, the memtransistor includes a substrate 110 having a first surface 111 and an opposite, second surface 112; a polycrystalline monolayer film 120 formed of an atomically thin material on the first surface 111 of the substrate 110; an electrode array having a plurality of electrodes 131-136 spatial-apart formed on the polycrystalline monolayer film 120 such that each pair of electrodes defines a channel 125 in the polycrystalline monolayer film 120 therebetween; and a gate electrode 140 formed on the second surface 112 of the substrate 110 and capacitively coupled with the channel 125. The polycrystalline monolayer film 120 contains grains defining a plurality of grain boundaries thereof, as shown in FIGS. 1B-1C for example. In certain embodiments, the grains have an average grain size of about 1-10 μm.

In certain embodiments, the atomically thin material comprises MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials.

In one embodiment, the substrate 110 is formed of SiO₂, or dielectrics including alumina, hafnia, or zirconia.

In certain embodiments, the gate electrode 140 is formed of highly doped Si, or other conductive materials.

In certain embodiments, each electrode 131/132/ . . . /136 of the electrode array is formed of a same metallic material or different metallic materials. In one embodiment, the electrode array is formed of at least one of Au, Ti, and other conductive materials.

In certain embodiments, the memtransistor is configured such that the Schottky barrier localized at each electrode is dynamically tunable so as to cause switching from a high resistance state (HRS) to a low resistance state (LRS) or from the LRS to the HRS in the memtransistor. In certain embodiments, the memtransistor is an LRS-HRS memtransistor or an LRS-LRS memtransistor.

In certain embodiments, the memtransistor combines resistive switching with transistor gating to realize nonlinear charge transport with wide tunability of individual states and switching ratios.

In certain embodiments, a switching mechanism of the memtransistor is characterizable with two memristors at the contacts connected by a field-effect transistor.

In certain embodiments, the grain boundaries in the polycrystalline monolayer film enable the memtransistor to have large switching ratios and prevent electrical breakdown by lowering the Schottky barriers through dynamic defect migration, and control devices on single grains of the polycrystalline monolayer film show a qualitatively different reversible breakdown phenomenon.

In certain embodiments, the memtransistor is fabricated in a field-effect geometry with channel lengths (L) and widths (W), each varying from 1 μm to 250 μm, as shown in FIGS. 1D-1E. In one embodiment, L=1-15 μm, and W=100-150 μm.

In another aspect of the invention, the memtransistor includes a polycrystalline monolayer film formed of an atomically thin material, where the polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof; and an electrode array formed on the polycrystalline monolayer film, wherein the electrode array has a plurality of electrodes electrically coupled with the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween. In certain embodiments, the grains have an average grain size of about 1-10 μm. In certain embodiments, the atomically thin material comprises MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials.

In certain embodiments, the memtransistor further includes a gate electrode capacitively coupled with the channel. In certain embodiments, the gate electrode is formed of highly doped Si, or other conductive materials.

In certain embodiments, the memtransistor further has a dielectric layer formed between the polycrystalline monolayer film and the gate electrode. In certain embodiments, the dielectric layer is formed of SiO₂ or dielectrics including alumina, hafnia, or zirconia.

In certain embodiments, the memtransistor is configured such that the Schottky barrier localized at each electrode is dynamically tunable so as to cause switching from an HRS to an LRS or from the LRS to the HRS in the memtransistor.

In certain embodiments, the memtransistor combines resistive switching with transistor gating to realize nonlinear charge transport with wide tunability of individual states and switching ratios.

In certain embodiments, a switching mechanism of the memtransistor is characterizable with two memristors at the contacts connected by a field-effect transistor.

In certain embodiments, the grain boundaries in the polycrystalline monolayer film enable the memtransistor to have large switching ratios and prevent electrical breakdown by lowering the Schottky barriers through dynamic defect migration, and control devices on single grains of the polycrystalline monolayer film show a qualitatively different reversible breakdown phenomenon.

In yet another aspect, the invention relates to a method for fabricating a memtransistor. The method includes growing a polycrystalline monolayer film on a substrate, where the polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof; and forming an electrode array on the grown polycrystalline monolayer film, wherein the electrode array has a plurality of electrodes electrically coupled with the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween.

In certain embodiments, the polycrystalline monolayer film is grown by chemical vapor deposition (CVD) on the substrates. In certain embodiments, the polycrystalline monolayer film comprises an atomically thin material of MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials. In certain embodiments, the substrate is formed of SiO₂, or dielectrics including alumina, hafnia, or zirconia.

In certain embodiments, the method further includes, prior to forming the electrode array on the grown polycrystalline monolayer film, coating a film of photoresist on the polycrystalline monolayer film to form a first structure; baking the first structure; exposing the first structure to UV light and developing the exposed first structure to form a second structure; patterning the second structure with a resist mask by reactive ion etching to form a third structure; and submerging the third structure in an N-Methyl-2-pyrrolidone (NMP) bath to remove the resist mask to form a patterned polycrystalline monolayer strips. Accordingly, the memtransistor is an LRS-LRS memtransistors.

In certain embodiments, the method further includes, prior to coating the film of photoresist on the polycrystalline monolayer film, coating a film of polymethylglutarimide (PMGI) on the polycrystalline monolayer film; and baking the coated film of PMGI on the polycrystalline monolayer film at about 170° C. for a period of time. Accordingly, the memtransistor is an LRS-HRS memtransistor.

In certain embodiments, the electrode array is formed by patterning a negative photoresist, followed by thermal evaporation of metals and lift-off in NMP.

In certain embodiments, the method further includes forming a gate electrode on the substrate such that the substrate is positioned between the gate electrode and the polycrystalline monolayer film, wherein the gate electrode is capacitively coupled with the channel. In certain embodiments, the gate electrode is formed of highly doped Si, or other conductive materials.

In one aspect, the invention relates to a circuitry has one or more memtransistors as disclosed above.

In another aspect, the invention relates to an electronic device has one or more memtransistors as disclosed above.

According to the invention, the multi-terminal memtransistor operates much like a neuron by performing both memory and information processing. With combined characteristics of a memristor and transistor, the memtransistor also encompasses multiple terminals that operate more similarly to a neural network. The multi-terminal memtransistor can be applied for, but are not limited to, the fields of artificial neuromorphic circuits with more than two syanpses; heterosynaptic plasticity; gate-tunable crossbar memristor arrays; and parallel computing via multi-terminals. The multi-terminal memtransistor enables more advanced neuromorphic circuits that better mimic the behavior of biological neurons than pre-existing devices, thus significantly advancing the prospects for neuromorphic computing, and has a great deal of advantages over conventional silicon complementary metal-oxide-semiconductor (CMOS) devices and memristors that may mimic very simple neural functions with 2 or 3 electrodes, whereas biological neurons have thousands of synapses for massively parallel computing.

In one exemplary implementation of the memtransistor, atomically thin molybdenum disulfide (MoS₂) with well-defined grain boundaries is used influence the flow of current. Similar to the way fibers are arranged in wood, atoms are arranged into ordered domains—called “grains”—within a material. When a large voltage is applied, the grain boundaries facilitate atomic motion, causing a change in resistance. Because MoS₂ is atomically thin, it is easily influenced by applied electric fields. This property allows one to make a transistor. The memristor characteristics come from the fact that the defects in the material are relatively mobile, especially in the presence of grain boundaries. The memristor previously reported by the co-inventors [20] uses individual, small flakes of MoS₂. However, the invented memtransistor makes use of a continuous film of polycrystalline MoS₂ that comprises a large number of smaller flakes. This enabled one to scale up the device from one flake to many devices across an entire wafer. When the length of the device is larger than the individual grain size, it is guaranteed to have grain boundaries in every device across the wafer. Thus, reproducible, gate-tunable memristive responses across large arrays of devices can be achieved.

After fabricating memtransistors uniformly across an entire wafer, additional electrical contacts are added. Typical transistors and memristor each have three terminals. According one embodiment of the invention, a seven-terminal device is realized, in which one terminal controls the current among the other six terminals. This is even more similar to neurons in the brain, because in the brain, one neuron is not usually connected to only one other neuron. Instead, one neuron is connected to multiple other neurons to form a network. The device structure according to the invention allows multiple contacts, which is similar to the multiple synapses in neurons. Accordingly, the memtransistor can be a foundational circuit element for new forms of neuromorphic computing.

These and other aspects of the present invention are further described in the following section. Without intending to limit the scope of the invention, further exemplary implementations of the present invention according to the embodiments of the present invention are given below. Note that titles or subtitles may be used in the examples for the convenience of a reader, which in no way should limit the scope of the invention. Moreover, certain theories are proposed and disclosed herein; however, in no way should they, whether they are right or wrong, limit the scope of the invention so long as the invention is practiced according to the invention without regard for any particular theory or scheme of action.

Multi-Terminal Memtransistor from Polycrystalline Monolayer MoS₂

In this exemplary embodiment, a 6-terminal memtransistor using polycrystalline monolayer MoS₂ is provided. The two-dimensional (2D) MoS₂ memtransistor shows gate tunability in individual states by 4 orders of magnitude in addition to large switching ratios with high cycling endurance and long-term retention of states. In addition to conventional neural learning behavior of long-term potentiation/depression, the 6-terminal MoS₂ memtransistor possesses gate-tunable heterosynaptic functionality that is not achievable using 2-terminal memristors. For example, the conductance between a pair of two floating electrodes (pre-synaptic and post-synaptic neurons) is varied by about 10 times by applying voltage pulses to modulatory terminals. In situ scanning probe microscopy, cryogenic charge transport measurements, and device modeling reveal that bias-induced MoS₂ defect motion drives resistive switching by dynamically varying Schottky barrier heights. Overall, the seamless integration of a memristor and transistor into one multi-terminal device has the potential to enable complex neuromorphic computing in addition to providing opportunities for studying the unique physics of defect kinetics in 2D materials.

In the embodiment, uniform polycrystalline monolayer MoS₂ films with an average grain size of 3-5 μm were grown by chemical vapor deposition (CVD) on SiO₂/Si substrates and characterized using X-ray photoelectron, photoluminescence, and Raman spectroscopies, as shown in FIGS. 1A-1C and 5A-5F. MoS₂ memtransistors were fabricated in a field-effect geometry with channel lengths (L) and widths (W) varying from 5 μm to 150 μm shown in FIGS. 1D-1F. Since clean interfaces between MoS₂ channels and metal electrodes were found to be critical, an unconventional photolithography process was developed based on a polymethylglutarimide (PMGI) and photoresist bilayer, as shown in FIGS. 6A-6D.

At large drain bias V_(D) in the sub-threshold regime (gate bias V_(G)<threshold voltage V_(th)), a typical memtransistor is in a high resistance state (HRS) for the V_(D) sweep from 0 to 80 V (sweep 1) and gradually changes to a low resistance state (LRS), as shown in FIG. 2A. The device maintains LRS during the sweep from 80 to 0 V (sweep 2), resets to HRS during the sweep from 0 to −80 V (sweep 3), and maintains HRS from −80 to 0 V (sweep 4). Thus, these devices act as LRS-HRS memtransistors. FIG. 2B shows that when V_(G) is varied from 50 to −50 V, both LRS and HRS resistances change by a factor of about 10⁴ and the switching ratio (I_(LRS)/I_(HRS) at V_(D)=0.5 V) is tuned from 300 to 8 (inset FIG. 2E). Due to the n-type MoS₂ channel, the forward-biased (V_(D)>0 V) device is completely OFF at V_(G)=−50 V, as shown in FIG. 2C, and the reverse-biased (V_(D)<0 V) device is insulating for a range of V_(D) depending on the applied V_(G)), as shown in FIGS. 2B and 7C. The gate leakage (I_(G)-V_(G)) remains below 200 pA during high V_(D) and V_(G) sweeps, as shown in FIG. 7A.

Unlike filament-based resistive switching, MoS₂ memtransistors do not require an electroforming process, although the switching ratio increases with increasing V_(D) sweep range, as shown in FIG. 7B. The largest switching ratio of greater than 10² was obtained from devices with W=100-150 μm and L=5-15 μm. The devices show bipolar resistive switching where reversing the bias polarity is essential to restoring the initial resistance states, as shown in FIGS. 7D-7E. The hysteresis in the I_(D)-V_(D) characteristics of these MoS₂ memtransistors is fundamentally distinct from commonly reported hysteresis in I_(D)-V_(G) curves due to oxide-related traps in field-effect transistors [23, 24]. Instead, the transfer characteristics (I_(D)-V_(G)) of MoS₂ memtransistors in LRS and HRS show significant shifts (about 10 V) in threshold voltage (V_(th)) with curves that cross each other at V_(G)=V_(cross), as shown in FIG. 2C. HRS shows up to 100 times higher resistance for V_(G)<V_(cross) and 2 times higher field-effect mobility (μ) at V_(G)>V_(cross) compared to LRS. Therefore, the forward bias switching loop changes from counterclockwise (LRS to HRS) for V_(G)<V_(cross) to clockwise (HRS to LRS) for V_(G)>V_(cross), as shown in FIGS. 2B and 7F.

FIG. 2D shows endurance characteristics for a MoS₂ memtransistor that was switched 475 times between LRS and HRS through full sweep cycles. Within a subset, I_(D) saturates to an upper value via stretched exponentials, as shown in FIGS. 7G-7K and 8A. Between neighboring subsets, I_(D) jumps randomly to an about 10 times smaller value followed by the same inverse exponential growth, which suggests an oxide-related trap-release process activated by large fields near the source electrode in forward bias [23]. This behavior is reduced under reverse-bias, as shown in FIG. 8B, possibly due to smaller band-bending near the drain electrode in reverse bias. Since both HRS and LRS show similar transitory decays, the switching ratio (about 100) remains relatively constant, as shown in FIG. 2D. Individual resistance states measured up to 24 hours show a projected retention of distinct states for timescales on the order of years, as shown in FIGS. 2E and 8E. A statistical study of 62 devices that were fabricated with identical geometry on a single chip showed a log-normal distribution of switching ratios, as shown in FIG. 2F. Device-to-device variability is attributed to spatial inhomogeneity in the CVD MoS₂ film.

Due to its 2D nature, the MoS₂ channel allows the switching mechanism to be probed via in situ electrostatic force microscopy (EFM) as shown in FIGS. 3A-3B. The drain contact and conductive cantilever tip were biased independently, as shown in FIGS. 9A-9O, while the cantilever phase shift was recorded as the tip traced the topography profile 50 nm above the surface. Since the phase shift is proportional to the square of the potential difference between the tip and the underlying surface, the phase image provides a map of the local potential [20]. Line profiles reveal a sharper potential drop (larger field) at the source in forward HRS compared to forward LRS, suggesting a larger contact resistance in HRS than LRS, as shown in FIG. 3B. Reverse HRS also shows a larger field at the drain compared to reverse LRS, although this difference is smaller, consistent with the smaller switching ratio at reverse bias. Multiple line profiles confirm that the differences in HRS and LRS electric fields are consistent along the entire channel width, despite grain boundary induced EFM phase variations away from the contacts, as shown in FIGS. 9G-9O. Since a reverse-biased Schottky diode at the source (drain) dominates I_(D) at V_(D)>0 (V_(D)<0), EFM measurements provide direct evidence that the HRS to LRS (LRS to HRS) switching in memtransistors is caused by dynamic tuning of Schottky barriers. Using variable temperature (T) charge transport measurements and assuming a 2D thermionic emission model, the effective barrier heights (Φ_(b)) in different states are extracted from the slope of ln(I/T^(3/2)) versus 1/T at different V_(G), as shown in FIGS. 10A-10D. Thermionic emission dominates at V_(G)<V_(FB) (flat-band voltage) producing linearly varying Φ_(b) with V_(G). Thermally-assisted tunneling through a deformed Schottky barrier begins to contribute at V_(G)>V_(FB), resulting in deviation from the linear trend, as shown in FIG. 3C. Thus, the Schottky barrier height (Φ_(sb)=Φ_(b)) is extracted from V_(G)=V_(FB). V_(FB) decreases from 2 V (HRS) to −8 V (LRS), consistent with a V_(th) shift of 15 V for the same device, as shown in FIGS. 10A-10D. In addition, Φ_(sb) decreases from 125 meV (HRS) to 80 meV (LRS), confirming the observations from EFM.

Charge transport in MoS₂ LRS-HRS memtransistors can be described by Schottky barrier transistors, e.g., equations (1) and (2) below, where Φ_(b) is a function an internal state variable (w) defined as the width of the region with excess dopants (Δn), as shown in FIG. 11A [1, 17, 25]. Tuning the Schottky barrier through increased doping near contacts (Φ_(b)˜√{square root over (Δn.w))} is a standard practice in conventional field-effect transistors [26, 27]. Similarly, we propose that defects in MoS₂ act as dopants with their local migration under an applied bias being facilitated by grain boundaries, as previously observed under transmission electron microscopy and explained by ab initio calculations [18, 19, 21]. Thus, we develop a memtransistor model where the effective Φ_(b) changes by image charge lowering and tunneling at high biases, resulting in the following coupled equations:

$\begin{matrix} {I_{D} = {D\mspace{14mu} {\exp \left( \frac{e\left( {V_{G} - V_{th}} \right)}{{c_{r}.k_{B}}T} \right)}\left( {1 - {\exp \left( {- \frac{{eV}_{D}}{k_{B}T}} \right)}} \right)\mspace{14mu} {\exp \left( \frac{\Phi_{b}(w)}{k_{B}T} \right)}}} & (1) \\ {{\Phi_{b}(w)} = {\varphi_{b\; 0} - {\frac{e}{ɛ_{s}}\sqrt{\frac{\Delta \; {n.w}}{4\pi}}} + {\sqrt{\frac{e}{4{\pi ɛ}_{s}}}\left( \frac{2{{en}\left( {\varphi_{b\; 0} + {A{V_{d}}}} \right)}}{ɛ_{s}} \right)^{1\text{/}4}}}} & (2) \\ {\frac{\partial w}{\partial t} = {{E.I_{D}}\left\{ {1 - \left\lbrack {\left( {w - 0.5} \right)^{2} + 0.75} \right\rbrack^{p}} \right\}}} & (3) \end{matrix}$

where A, D, E, and ϕ_(b0) are fitting parameters, and e, n, ε_(s) are electronic charge, doping level, and dielectric constant of monolayer MoS₂, respectively. Equation (3) captures the non-linear kinetics of the dopants near the contacts using a window function where the degree of non-linearity is defined by a positive integer p [28]. This model agrees well with the experimental data, as shown in FIGS. 2A and 11A-11E, and helps establish that the dependence of w on V_(G) (through I_(D)) embodies the most essential feature of the MoS₂ memtransistor and distinguishes it from a 2-terminal memristor [17]. To further illustrate the non-trivial switching, we fabricated MoS₂ devices without the PMGI-based process and used residual about 1.5 nm thick photoresist layer as a tunneling barrier between MoS₂ and the metal contacts, as shown in FIGS. 3D-3E and 12A-12E. The tunneling barrier de-pins the Fermi level and causes the resistance states to change abruptly upon crossing 0 V, resulting in LRS-LRS memtransistors. Overall, the switching mechanism of both LRS-HRS and LRS-LRS memtransistors can be described by two memristors at the contacts connected by a field-effect transistor, as shown in FIG. 12E.

While grain boundaries in polycrystalline MoS₂ memtransistors enable large switching ratios and prevent electrical breakdown by lowering Schottky barriers through dynamic defect migration, control devices on single grains of CVD-grown MoS₂ show a qualitatively different reversible breakdown phenomenon, as shown in FIG. 4A. This breakdown event is marked by a sharp drop in the conductance at a voltage V_(br) during sweep 1 that increases again to the original value during sweep 2. This abrupt change in charge transport is accompanied by the emergence of dendritic features (about 300-500 nm) close to the source, as shown in upper inset in FIG. 4A and in FIGS. 13A-13B. Control devices reveal a linear correlation of breakdown current (I_(br)) with the width of the source electrode (W_(src)) and no correlation with L, as shown in lower inset in FIG. 4A and in FIGS. 13F-13J. Since I_(D) normally scales as W/L, the observed deviation in this scaling at breakdown suggests that the reverse-biased Schottky diode at the source electrode creates a bottleneck for electron injection at the channel [27], ultimately causing electromigration at the source contact [7]. This reversible breakdown in CVD MoS₂ contrasts the irreversible breakdown in exfoliated MoS₂ by Joule heating [29]. In the high bias limit (±120 V), polycrystalline MoS₂ memtransistors also degrade irreversibly in a manner that shows light emission during each subsequent sweep, as shown in FIGS. 13C-13E.

The 2D planar geometry of the MoS₂ memtransistor provides a platform to realize multi-terminal neural circuits mimicking multiple synaptic connections in neurons. For example, in a 6-terminal memtransistor, the conductance between any permutation of two of the four inner electrodes can be modulated by high-bias pulses applied to the outer two electrodes while the inner electrodes are kept floating, as shown in FIGS. 4B and 14A-14H. To achieve hetero synaptic plasticity, the conductance between pre-synaptic and post-synaptic neurons should be controlled by additional modulatory terminals [30]. While this type of modulation has been shown previously in Ag-based cationic memristors, this design is limited to only 3 terminals due to the requirement of filament formation across the channel [6, 30]. In contrast, the MoS₂ memtransistor enables larger numbers of terminals and facile tuning via modulation of the Schottky barrier localized at each terminal. Multi-terminal memtransistors also allow further tuning of heterosynaptic plasticity via a gate electrode where the switching ratio between any permutation of side electrodes can be controlled from about 2 to 10-fold by varying V_(G) from 50 to 20 V, as shown in FIG. 14F.

The MoS₂ memtransistor also demonstrates long-term potentiation and long-term depression that mimic excitatory and inhibitory synapses in organisms, as shown in FIG. 4C. Post-synaptic current (PSC) is shown to increase and decrease exponentially with repetition of positive and negative bias pulses of 1 msec duration, as shown in FIG. 4C. The linearity of pulse training is comparable to metal-oxide memristors and can be further improved by employing bipolar pulsing schemes [11, 31]. Mimicking an indirect spike-timing dependent plasticity (STDP), paired pulses separated by a time interval (Δt) induce positive and negative changes in synaptic weight with positive and negative pulses, as shown in FIG. 4D, resulting in time constants of about 2 and 6 msec, respectively, which are comparable to biological synapse response times [11, 32].

According to the invention, the MoS₂ memtransistor combine resistive switching with transistor gating to realize nonlinear charge transport with wide tunability of individual states and switching ratios. In contrast to conventional devices that require single-crystal MoS₂ flakes, the utilization of polycrystalline and all-surface MoS₂ films allows straightforward scaling of this technology to large-area integrated circuits and post-growth defect engineering. The 2D planar geometry of monolayer MoS₂ further enables the realization of multi-terminal memtransistors with unprecedented heterosynaptic plasticity that holds promise for complex Hebbian learning from multiple inputs in neuromorphic computing by mimicking biological neurons with multiple synapses.

Fabrication and characterization of the MoS₂ memtransistor according to certain embodiments of the invention are described in detail as follows.

Chemical Vapor Deposition of MoS₂ Film

Polycrystalline monolayer MoS₂ with continuous film coverage was directly grown on oxidized Si substrates by chemical vapor deposition (CVD) using sulfur powder (Sigma-Aldrich) and molybdenum trioxide powder (MoO₃, 99.98% trace metal Sigma-Aldrich) following the recipe reported earlier [1, 2]. Prior to growth, Si substrates were bath-sonicated for about 10 min in acetone and isopropyl alcohol (IPA) and subsequently cleaned under O₂ plasma (Harrick Plasma) at about 200 mTorr for about 2 min with about 10.2 W power applied to the RF coil. The substrates were placed downstream in close proximity to about 12 mg of MoO₃ powder in an alumina boat in an about 1 inch diameter quartz tube furnace (Lindberg/Blue). About 150 mg of sulfur powder in an alumina boat was placed about 30 cm upstream of the MoO₃ boat (outside the furnace) and was heated independently using a temperature-controlled heating belt. The tube furnace was purged using ultrahigh purity Ar gas at about 200 sccm for about 10 min. Then, the pressure was increased to about 400 Torr, and the tube was evacuated to its base pressure of about 60 mTorr. The purging process was repeated twice to achieve an inert growth environment. The pressure was kept at about 150 Torr with an about 25 sccm flow of Ar gas during growth and cool down. Following the purge process, the furnace was heated to about 150° C. in about 5 min and held at that temperature for about 20 min to remove physisorbed contaminants from the growth environment. The furnace was then heated to about 800° C. at a rate of about 12° C./min and held at that temperature for 20 min, followed by natural cool down to room temperature. Concurrently, the heating belt around sulfur boat was first ramped to about 50° C. in about 5 min and was held at that temperature for 49 min. The heating belt was then brought to about 150° C. at a rate of about 4.5° C./min and held at that temperature for an additional about 23 min, after which it was allowed to cool down to room temperature naturally.

Chemical Characterization of Monolayer MoS₂ Film

Coverage and growth quality of continuous polycrystalline monolayer CVD MoS₂ on about 5 mm×5 mm substrates were characterized by optical microscopy, Raman microscopy, and photoluminescence (PL) spectroscopy. Raman spectra collected from a Horiba Scientific XploRA PLUS Raman microscope, as shown in FIG. 5A, show a peak spacing of about 19 cm⁻¹ between in-plane A_(1g) and out-of-plane E¹ _(2g) breathing modes, thus confirming monolayer MoS₂ [3]. PL spectroscopy, as shown in FIG. 5B, shows a dominant exciton A at about 673 nm, typical of CVD-grown monolayer MoS₂ on SiO₂.

The chemical composition of CVD-grown polycrystalline monolayer MoS₂ films was confirmed by X-ray photoelectron spectroscopy (XPS) measurements using a Thermo Scientific ESCA Lab 250Xi scanning XPS connected with a monochromatic K-alpha Al X-ray line. The X-ray beam size was approximately 900 μm in diameter with an elliptical cross-section. A charge neutralization Ar⁺ ion flood gun was also used to compensate for local electrostatic fields arising from charge build up in the MoS₂/SiO₂ samples. All XPS spectra were analyzed using Advantage software (Thermo Scientific). All Mo 3d subpeaks were fit using floating Gaussian-Lorentzian mixing and modified Shirley background subtraction. Fitting of Mo 3d subpeaks ensured that their full-width at half-maximum (FWHM) values were less than 3 eV, and doublets were also constrained to have the same FWHM. Charging effects were compensated in XPS spectra analyses by correcting all spectra against the C 1s adventitious carbon peak at 284.8 eV. As shown in FIGS. 5C-5D, the XPS spectra of the Mo 3d and S 2p orbitals are consistent with previous reports [4] of stoichiometric CVD MoS₂ with a minor amount of MoO_(x) within the MoS₂ film [1].

Scanning Probe Microscopy

CVD MoS₂ films were characterized by atomic force microscopy (AFM) in ambient conditions using an Asylum Cypher AFM system in lateral force microscopy (LFM) mode and tapping mode. For LFM, NanoWorld FMR cantilevers with a resonant frequency of about 75 kHz and contact force of about 5 nN were used, as shown in FIG. 1C. The LFM retrace image was acquired by scanning the tip from right to left with a contact force of about 5 nN and scan rate of 1 Hz. For tapping mode, NanoWorld NCHR-W Si cantilevers (resonant frequency about 320 kHz) were used, as shown in FIGS. 5E-5F. A step height of 0.73 nm at the edge of a MoS₂ flake confirms monolayer thickness. AFM measurements of individual flake devices after electrical breakdown, as shown in upper inset in FIG. 4A and in FIGS. 13A-13J, were conducted in tapping mode using a Bruker Dimension FastScan® AFM. Electrostatic force microscopy (EFM) of MoS₂ memtransistors was conducted in ambient conditions using the environment cell of the Asylum Cypher AFM system using NanoWorld PointProbe EFM tips coated with Par (resonant frequency of about 75 kHz).

Fabrication of MoS₂ Memtransistors

MoS₂ LRS-HRS memtransistors were fabricated following a photolithography process developed to minimize processing residues. First, a film of polymethylglutarimide (PMGI) was spin-coated on SiO₂/Si substrates covered by polycrystalline monolayer MoS₂ at about 4500 rpm for about 45 sec followed by a baking step for about 10 min at about 170° C. using a hot plate. Note that the baking conditions for the PMGI layer were found to be critical. Lower temperature (about 160° C.) resulted in delamination during development while higher temperature (about 180° C.) made it difficult to remove PMGI during the lift-off step. Afterwards, a thin film of photoresist (S1813, Shipley Company) was spin-coated at about 4000 rpm for about 1 min followed by another pre-baking step at about 115° C. for about 1 min. The bilayer resist was exposed to UV light (about 365 nm) for about 15 sec and then developed in MF319 developer (Shipley Company) for about 20 sec without further post-baking. The samples were rinsed with DI water and thoroughly dried before subjecting them to reactive ion etching to pattern the exposed MoS₂ film. The MoS₂ film was etched using Ar at power of about 50 W, pressure of about 100 mTorr, and flow rate of about 50 sccm for about 20 sec. Subsequently, the bilayer resist mask was removed by submerging the substrate overnight in an N-Methyl-2-pyrrolidone (NMP) bath heated at about 80° C. At this stage, the patterned MoS₂ strips resemble the optical image shown in FIG. 1E. Finally, source-drain electrodes were fabricated by patterning a negative photoresist NR9-1000PY (Futurrex, Inc.) followed by thermal evaporation of metals (about 3 nm Ti/50 nm Au) and lift-off in NMP. MoS₂ LRS-LRS memtransistors were fabricated using the same recipe except that no PMGI layer was used.

Electrical Measurements

All room temperature electrical measurements were carried in a vacuum probe station at a pressure of about 5×10⁻⁵ Ton in dark using a LakeShore CRX 4K probe station. Endurance, retention, and neural learning tests were conducted in vacuum using Pulse Measure Units in a Keithley 4200A-SCS Parameter Analyzer and home-developed LabVIEW programs. For variable temperature transport measurements, the devices were first switched to HRS and I_(D)-V_(G) characteristics were collected at V_(D)=0.1 V from about 300 K to about 75 K at a step of about 25 K. A pressure of about 8×10⁻⁷ Ton was achieved during cryogenic measurements using a built-in cryopump. The devices were allowed to heat up to room temperature overnight and then switched to LRS at room temperature followed by similar variable temperature transport measurements in LRS. In the sub-threshold regime, the charge transport in Schottky barrier field-effect transistors is dominated by thermionic emission [5, 6]:

$\begin{matrix} {I_{D} = {{A^{*}.T^{\frac{3}{2}}}\mspace{14mu} {{\exp \left( \frac{\varphi_{b}}{kT} \right)}\left\lbrack {{\exp \left( \frac{{eV}_{D}}{kT} \right)} - 1} \right\rbrack}}} & (4) \end{matrix}$

where A*, k, e, T, and ϕ_(b) are the 2D equivalent Richardson constant, the Boltzmann constant, electronic charge, temperature, and Schottky barrier height, respectively. The term T^(3/2) comes from the 2D model (as opposed to T² in 3D). At low bias, we can neglect V_(D) and extract ϕ_(b) from ln(I/T^(3/2)) versus 1/T at different V_(G), as shown in FIGS. 10A-10D.

Modeling the MoS₂ Memtransistor

We model the memtransistor behavior by integrating a mathematical formalism of memristive systems [7-10] and memory transistors (memtransistors) [11] with the charge transport model of a Schottky barrier field-effect transistor (SB-FET) [5, 12-16]. Memristive systems are defined as:

$\begin{matrix} {{\frac{dw}{dt} = {f\left( {w,v,t} \right)}},{I = {{g\left( {w,v,t} \right)}.v}}} & (5) \end{matrix}$

where t is time, and v and I are the input and output of the system, respectively; w is an internal state variable represented by a n-dimensional vector; g is a continuous scalar function; while f is a continuous n-dimensional vector function. Note that lower case symbols are used throughout this section to enhance clarity. Subsequently, a voltage-controlled memtransistor is defined [11] as

$\begin{matrix} {{\frac{dw}{dt} = {f\left( {w,v_{g},v_{d}} \right)}},{i_{d} = {g\left( {w,v_{g},v_{d}} \right)}},{i_{g} = {h\left( {w,v_{g},v_{d}} \right)}},} & (6) \end{matrix}$

where v_(d) and v_(g) are input drain and gate voltages, and i_(d) and i_(g) are measured drain and gate currents; g and h are scalar functions whereas f is a n-dimensional vector determined by the dimension of the vector state variable w. The dependence on time t is implicit through the voltage sweep rates. In 1^(st) order memristors, w is a scalar and is usually defined by the physical region of devices including higher concentration of charged dopants or vacancies. Similarly, floating gate metal-oxide-semiconductor field-effect transistors (MOSFETs) [17] and nanoionic dielectric gated FETs [18] have also been treated as 1^(st) order memtransistors where f is a scalable function [11].

In the present MoS₂ memtransistors, EFM and cryogenic transport measurements show strong evidence of dynamic variation in Schottky barrier height. Indeed, Schottky barrier modulation is the underlying mechanism of interface-based switching in transition-metal oxide and ferroelectric memristors where local segregation of mobile dopants varies the tunneling barrier dynamically [19-25]. Tuning the Schottky barrier by ion-implantation (i.e., local density of dopants) is central to the contact engineering in FETs [5, 12-14]. Based on these observations, we hypothesize that the local redistribution of dopants in polycrystalline MoS₂, facilitated by grain boundaries, is the main cause of barrier modulation. Varying the density of dopants (n₁) in the region w from the contact edge, as shown in FIG. 13A, changes the maximum electric field ξ_(m) (and effective Schottky barrier height Δϕ_(image1)) by virtue of image charge lowering [5] as

$\begin{matrix} {{\xi_{m}} = {{\frac{e}{ɛ_{s}}\left( {{n_{1}w} - {n\left( {d - w} \right)}} \right)} \approx \frac{{en}_{1}w}{ɛ_{s}}}} & (7) \\ {{\Delta\varphi}_{{image}\; 1} \approx {\frac{e}{ɛ_{s}}\sqrt{\frac{n_{1}w}{4\pi}}}} & (8) \end{matrix}$

where e is electronic charge, and ε_(s) is dielectric constant of the semiconductor. In the case of a 2D semiconductor, the metal image plane is cut by half, and thus the equation for a bulk semiconductor changes only by a factor of 2 that is neglected here since n₁ is a fitting parameter. However, image charge lowering also depends on drain bias v_(d) and gate bias v_(g) and cannot be neglected at large biases. As shown previously [5, 15, 16], the easiest way to incorporate the high bias scenario is through geometrical factors A and B, resulting in

$\begin{matrix} {{\Delta\varphi}_{{image}\; 2} = {\sqrt{\frac{e\; \xi_{m}}{4{\pi ɛ}_{s}}} = {\sqrt{\frac{e}{4{\pi ɛ}_{s}}}\left\lbrack {\sqrt{\frac{B\left( {v_{g} - v_{th}} \right)}{t_{ox}}} + \sqrt[4]{\frac{2{{en}\left( {\varphi_{b\; 0} + {Av}_{d}} \right)}}{ɛ_{s}}}} \right\rbrack}}} & (9) \end{matrix}$

where v_(th) is threshold voltage and t_(ox) is thickness of oxide dielectric. Furthermore, at high biases tunneling cannot be neglected and its essential feature can be captured in the following expression [15]:

$\begin{matrix} {{\Delta\varphi}_{tunnel} = {\frac{1}{e}\left( \frac{3e\; {\hslash \left( {\ln \mspace{14mu} 2} \right)}}{4\sqrt{2m^{*}}} \right)^{2\text{/}3}\left( \frac{B\left( {v_{g} - v_{th}} \right)}{t_{ox}} \right)^{2\text{/}3}}} & (10) \end{matrix}$

where m* is the effective mass and ℏ is the Planck constant. The net effective barrier height (Δϕ) can be obtained by adding equations (8)-(10) to obtain

$\begin{matrix} {\mspace{76mu} {{\Delta\varphi} = {{\Delta\varphi}_{{image}\; 1} + {\Delta\varphi}_{{image}\; 2} + {\Delta\varphi}_{tunnel}}}} & (11) \\ {{\Delta\varphi} = {{\frac{e}{ɛ_{s}}\sqrt{\frac{n_{1}w}{4\pi}}} + {\sqrt{\frac{e}{4{\pi ɛ}_{s}}}\left\lbrack {\sqrt{\frac{B\left( {v_{g} - v_{th}} \right)}{t_{ox}}} + \sqrt[4]{\frac{2{{en}\left( {\varphi_{b\; 0} + {Av}_{d}} \right)}}{ɛ_{s}}} + {\frac{1}{e}\left( \frac{3e\; {\hslash \left( {\ln \mspace{14mu} 2} \right)}}{4\sqrt{2m^{*}}} \right)^{2\text{/}3}{\left( \frac{B\left( {v_{g} - v_{th}} \right)}{t_{ox}} \right)^{2\text{/}3}.}}} \right.}}} & (12) \end{matrix}$

A dynamically varying barrier changes the transistor i_(d)-v_(d) characteristics to yield a pinched hysteresis loop. Since memristive switching ratio is largest in the sub-threshold regime, as shown in FIG. 2B, we take the following expression for i_(d)-v_(d) characteristics for SB-FETs [26]:

$\begin{matrix} {i_{d} = {D\mspace{14mu} {\exp \left( \frac{e\left( {v_{g} - v_{th}} \right)}{c_{r}.{kT}} \right)}\left( {1 - {\exp \left( {- \frac{{ev}_{d}}{kT}} \right)}} \right)}} & (13) \end{matrix}$

where the first exponential term gives a straight line in log-linear plot of i_(d)-v_(g) characteristics, as shown in FIG. 2C, and the corresponding (sub-threshold) slope is given by

$2.3\frac{kT}{e}{c_{r}.}$

The second exponential term is responsible for the large asymmetry observed in high-bias characteristics, as shown in FIG. 2A. The second term becomes negligible for v_(d)>3 kT, and thus forward bias characteristics saturate quickly with v_(d), as shown in FIG. 2B. Since the variable temperature conductivity fits well to the thermionic emission model, as shown in FIG. 3C, in the sub-threshold regime (v_(g)<v_(th)), we obtain the voltage-controlled memtransistor equation by multiplying equation (10) with a barrier height term in the thermionic equation (4):

$\begin{matrix} {i_{d} = {D\mspace{14mu} {\exp \left( \frac{e\left( {v_{g} - v_{th}} \right)}{c_{r}.{kT}} \right)}\left( {1 - {\exp \left( {- \frac{{ev}_{d}}{kT}} \right)}} \right){\exp \left( \frac{\varphi_{b}(w)}{kT} \right)}}} & (14) \end{matrix}$

For v_(d)>0 V, the Schottky diode at the source is reverse biased and acts as bottleneck for device current, whereas, for v_(d)<0 V, the Schottky diode at the drain is reverse biased. Therefore, dopant redistribution at the two different contacts dominates in the positive and negative bias regimes, allowing the device to be visualized as two memristors connected by a transistor, as shown in FIG. 12E. Local electrostatics at the two contacts is inherently asymmetric at large positive and large negative v_(d) values because v_(g)-v_(s)<0 V at the source for v_(d)>0 V (note, v_(s)=0 V); while, v_(g)-v_(d)>0 V at the drain for v_(d)<0 V in the most relevant regime of v_(g)<0 V and |v_(d)|>|v_(g)|. In other words, the MoS₂ Fermi level is deeper into the band gap at the source in forward bias than that at the drain in reverse bias. Since both v_(d) and v_(g) dictate Schottky barrier modulation, we need two different sets of equations for source and drain in forward and reverse biases, respectively. Neglecting gate leakage current i_(g), as shown in FIG. 7A, we modify equation (6) to get the following equation (15), where the only differences between functions f and g, and between h and i, are the fitting parameters. w_(d) and w_(s) are state variables at the drain and source contacts, respectively.

$\begin{matrix} {{\frac{\partial w_{d}}{\partial t} = {f\left( {w_{d},v_{d},v_{g},t} \right)}},{\frac{\partial w_{s}}{\partial t} = {g\left( {w_{s},v_{d},v_{g},t} \right)}},{i_{d} = \left\{ {{\begin{matrix} {{{h\left( {w_{s},v_{d},v_{g},t} \right)}\mspace{14mu} {for}\mspace{14mu} v_{d}} \geq 0} \\ {{{i\left( {w_{d},v_{d},v_{g},t} \right)}\mspace{14mu} {for}\mspace{14mu} v_{d}} < 0} \end{matrix}i_{g}} = 0} \right.}} & (15) \end{matrix}$

Dynamic redistribution of dopants under bias is usually governed by drift motion. Consequently, physical models of memristors often require a non-linear drift with field to keep the state variable w within the boundary conditions. Dopant drift is significantly suppressed as it approaches the device dimension on either side, thereby avoiding irreversible hard switching or breakdown. Non-linearity of dopant drift is usually modeled by a window function F(w), and thus we obtain [10]:

$\begin{matrix} {\frac{\partial w}{\partial t} = {\frac{\mu \; R_{on}{i(t)}}{D^{2}}{F(w)}}} & (17) \end{matrix}$

where D is the distance between the two electrodes, μ is the mobility of dopant, and R_(on) is the resistance of the device when w spans the whole distance D. The window function [27]

F(w)=1−[(w−0.5)²+0.75]^(p)   (18)

has reproduced bipolar resistive switching in a wide range of metal-oxide memristors. It should be noted that larger p values imply larger non-linearity. Thus, we combine equations (12), (14), (15), and (17) to get the following set of equations for v_(d)>0 V:

$\begin{matrix} {i_{d} = {D\mspace{14mu} {\exp \left( \frac{e\left( {v_{g} - v_{th}} \right)}{c_{r}.{kT}} \right)}\left( {1 - {\exp \left( {- \frac{e{v_{d}}}{c_{vd}.{kT}}} \right)}} \right){\exp\left( \frac{\varphi_{b\; 0} - {\frac{e}{ɛ_{s}}\sqrt{\frac{n_{1}w_{d}}{4\pi}}} + {\sqrt{\frac{e}{4{\pi ɛ}_{s}}}\sqrt[4]{\frac{2{{en}\left( {\varphi_{b\; 0} + {A{v_{d}}}} \right)}}{ɛ_{s}}}}}{kT} \right)}}} & (18) \\ {\mspace{76mu} {\frac{\partial w_{d}}{\partial t} = {E.{i_{d}\left( {1 - \left\lbrack {\left( {w_{d} - 0.5} \right)^{2} + 0.75} \right\rbrack^{p}} \right)}}}} & (19) \\ {\mspace{76mu} {v_{d} = \left\{ \begin{matrix} {{5t}\mspace{124mu}} & {{{{for}\mspace{14mu} t} = {0\text{-}16\mspace{14mu} s}}\mspace{11mu}} \\ {80 - {5\left( {t - 16} \right)}} & {{{for}\mspace{14mu} t} = {16\text{-}32\mspace{14mu} s}} \end{matrix} \right.}} & (20) \end{matrix}$

where equation (20) is the drain bias sweep and A, D, E and n₁ are fitting parameters. The geometrical factor c_(vd) plays a similar role as c_(r) and limits exponentially growing current at high negative biases. Here, we first focus on fitting i_(d)-v_(d) characteristics for a fixed v_(g); therefore, the terms involving geometrical factor B in equation (12) are absorbed in the fitting parameter D. Similarity the following set of equations describes the memtransistor behavior for v_(d)<0 V,

$\begin{matrix} {i_{d} = {D^{\prime}\mspace{14mu} {\exp \left( \frac{e\left( {v_{g} - v_{th}} \right)}{c_{r}.{kT}} \right)}\left( {1 - {\exp \left( {- \frac{e{v_{d}}}{c_{vd}.{kT}}} \right)}} \right){\exp\left( \frac{{\varphi\prime}_{b\; 0} - {\frac{e}{ɛ_{s}}\sqrt{\frac{n_{1}w_{d}}{4\pi}}} + {\sqrt{\frac{e}{4{\pi ɛ}_{s}}}\sqrt[4]{\frac{2{{en}\left( {\varphi_{b\; 0} + {A{v_{d}}}} \right)}}{ɛ_{s}}}}}{kT} \right)}}} & (21) \\ {\mspace{76mu} {\frac{\partial w_{s}}{\partial t} = {E^{\prime}.{i_{d}\left( {1 - \left\lbrack {\left( {w_{s} - 0.5} \right)^{2} + 0.75} \right\rbrack^{p}} \right)}}}} & (22) \\ {\mspace{76mu} {v_{d} = \left\{ \begin{matrix} {{{- 5}\left( {t - 32} \right)}\mspace{56mu}} & {{{for}\mspace{14mu} t} = {32\text{-}48\mspace{14mu} s}} \\ {{- 80} + {5\left( {t - 48} \right)}} & {{{for}\mspace{14mu} t} = {48\text{-}64\mspace{14mu} s}} \end{matrix} \right.}} & (23) \end{matrix}$

where a different set of fitting parameters, A′, D′, and E′ are needed due to asymmetric electrostatics and dopant kinetics.

The experimental memtransistor characteristics are fit well with this model, as shown in FIG. 2A, FIGS. 11B-11C show dynamic modulation of w_(d) and w_(s) with v_(d). Experimental values of c_(r)=83.3 and v_(th)=20 V were used in addition to the constant ϕ_(b0)=385 meV and ε_(s)=4 for monolayer MoS₂ [28]. The fitting parameters in FIG. 2A are A=10⁻⁵, D=5.5×10⁻⁹, and E=7×10⁴. Note that although we treated w and n₁ independently in the mathematical formalism, we cannot measure them independently. Thus, we treat the product (n₁.w) as an internal state variable. For the fitting in FIG. 2A, we get n₁.w_(s)<10¹⁰ cm⁻² and n₁.w_(s)<3.5×10⁹ cm⁻² in order to get Schottky barrier heights covering the entire range of the experimental values (80-125 meV) shown in FIG. 3C (n₁ in the model has units of cm⁻³). Fitting in FIG. 2A results in effective Schottky barrier heights ranging from 20 meV to 280 meV in LRS and HRS, respectively. Thus, overestimation of the simulated values in HRS and underestimation in LRS could result from non-idealities in the transistor transport model at high biases. Assuming w of order of a few nanometers, we get a maximum excess doping n₁ about 10¹⁰ cm⁻² that is within the range of measured doping from MoS₂ defects [4].

The smaller value of n₁.w_(d) compared to n₁.w_(s) results from smaller fields at the drain for v_(d)<0 V than that at source for v_(d)>0 V, consistent with the smaller hysteretic loop in reverse bias. Note that although the net device current (i_(d)) is determined by w_(s) for v_(d)>0 V and by w_(d) for v_(d)<0 V, w_(d) (w_(s)) must return to its initial value during v_(d)>0 V (v_(d)<0 V) for reversible behavior. Achieving this behavior is trivial by setting appropriate fitting parameters D, E (D′, E′). In real devices, a large electric field is also expected near forward biased Schottky diodes and redistribution of dopants to the initial configuration is expected. Finally, by considering the first exponential term consisting of v_(g), we can simulate the gate-tunability of memtransistor characteristics consistent with the observed experimental behavior, as shown in FIGS. 11D-11E. Deviations between simulations and experiments become larger at larger v_(g) values due to the decreased validity of the SB-FET model beyond the sub-threshold regime.

Switching Mechanism

The switching mechanism of MoS₂ memtransistors can be understood by assuming two memristors at the source (S-memristor) and the drain (D-memristor) that are connected by a FET, as shown in FIG. 12E. Note that the gate-tunable resistive switching cannot be obtained by simply connecting two conventional memristors with a transistor. The Schottky barrier height modulation is intimately connected to the operation of the SB-FET in the MoS₂ memtransistor. Thus, this distinction of memristor and transistor only serves to clarify the switching mechanism. MoS₂ memtransistors with residue-free interfaces between the metal and MoS₂, as shown in FIGS. 2A-2F, undergo HRS to LRS switching at positive bias and from LRS to HRS in negative bias and are called “LRS-HRS” memtransistors here. MoS₂ memtransistors with about 1.5 nm polymer tunnel barrier between metal and MoS₂, as shown in FIGS. 12A-12D, undergo similar HRS to LRS switching at both positive and negative biases and are called “LRS-LRS” memtransistors. The main difference is that the LRS-HRS memtransistor retains its state while crossing over 0 V, whereas LRS-LRS memtransistors undergo switching while crossing over 0 V, as shown in FIGS. 2B and 3D. Both of the contrasting behaviors can be explained by the resistance table shown in FIG. 12E. HD and LD are the resistance values of HRS and LRS of the D-memristor, whereas HS and LS are the resistance values of HRS and LRS of the S-memristor. We have HD>>LD and HS>>LS for both kinds of memtransistors, and their relative amplitudes determine the switching ratio. LD′ and LS′ are intermediate states whose values differ vastly between LRS-HRS and LRS-LRS memtransistors.

For LRS-HRS memtransistors, switching events A and B dominate while the switching event C is negligible, as shown in FIG. 12E. Switching A occurs at the bottleneck contact (i.e., the source for forward bias and the drain for reverse bias) while switching B occurs at the other contact in order to restore the dopant distribution at the end of a full sweep cycle. This condition is necessitated by bipolar resistive switching, and its physical origin is well-explained by the memtransistor model. Thus, intermediate states LD′ and LS′ have values close to LD and LS, respectively.

On other hand, for LRS-LRS memtransistors, all switching events A, B, and C dominate. The resist layer acts at a tunnel barrier and de-pins the Fermi level of MoS₂. Similar Fermi level de-pinning and has been shown in MoS₂ by employing ultrathin tunnel barriers such as 2 nm MgO [6], 1 nm TiO₂ [29], 1.5 nm Ta₂O₅ [30], and 0.6 nm hexagonal boron nitride [31], resulting in reduction of the effective Schottky barrier height (Δϕ_(b)) from 100 meV to 23 meV, from 121 meV to 27 meV, from 95 meV to 29 meV, and from 159 meV to 31 meV, respectively. Introduction of the tunnel barrier significantly increases the thermionic emission contribution to the total current, outweighing the additional tunnel resistance. Here, a about 1.5 nm thick tunnel barrier of the polymer resist makes the resistances of reverse-biased Schottky diodes at the source (V_(D)>0 V) and drain (V_(D)<0 V) more symmetric, resulting in more symmetric I_(D)-V_(D) compared to LRS-HRS memtransistors, as shown in FIGS. 2B and 3D. This switching involves a dynamic negative differential resistance feature for V_(D)<0 V common in memristors, as shown in FIG. 3D, [25]. This phenomena increases the resistance of the intermediate states LD′ and LS′ such that LD′>>LD, LS′>>LS. In other words, the switching B in FIG. 12E cannot be neglected, explaining the full switching cycles of LRS-LRS memtransistors. Compared to LRS-HRS memtransistors, LRS-LRS memtransistors show higher conductivity at the same V_(D) bias and switch at smaller V_(G) bias. This behavior can be explained by the smaller contact resistance from the de-pinned Fermi level and/or increased doping from the residue layer.

Comprehensive understanding of the LRS-HRS memtransistor also sheds light on the operating mechanism of the heterosynaptic multi-terminal devices, as shown in FIG. 4B. Conductance changes between the side electrodes 1-4 upon high bias pulses between the main electrodes 5 and 6 occurs due to modulation of the Schottky barrier near the side electrodes. Switching ratios were observed to increase with overlap areas of the side electrode with the MoS₂. Thus, floating electrodes pin the Fermi level of MoS₂, and the energy level of MoS₂ under the side electrodes is lower than the MoS₂ region outside the side electrodes, as shown in FIGS. 14G-14H, resulting in additional band-bending in the channel. Dopants are expected to redistribute near the floating electrodes in the same manner as LRS-HRS memtransistors during sweeps 2 and 4, as shown in FIG. 2A.

The foregoing description of the exemplary embodiments of the invention has been presented only for the purposes of illustration and description and is not intended to be exhaustive or to limit the invention to the precise forms disclosed. Many modifications and variations are possible in light of the above teaching.

The embodiments were chosen and described in order to explain the principles of the invention and their practical application so as to enable others skilled in the art to utilize the invention and various embodiments and with various modifications as are suited to the particular use contemplated. Alternative embodiments will become apparent to those skilled in the art to which the present invention pertains without departing from its spirit and scope. Accordingly, the scope of the present invention is defined by the appended claims rather than the foregoing description and the exemplary embodiments described therein.

LIST OF REFERENCES

-   [1]. Strukov, D. B., Snider, G. S., Stewart, D. R. & Williams, R. S.     The missing memristor found. Nature453, 80-83 (2008). -   [2]. Yang, J. J. et al. Memristive switching mechanism for     metal/oxide/metal nanodevices. Nat. Nanotechnol. 3, 429-433 (2008). -   [3]. Duygu, K., Shimeng, Y. & Wong, H. S. P. Synaptic electronics:     materials, devices and applications. Nanotechnology 24, 382001     (2013). -   [4]. Yu, S. & Chen, P. Y. Emerging memory technologies: Recent     trends and prospects. IEEE Sol. Stat. Circuit Mag. 8, 43-56 (2016). -   [5]. Yang, J. J., Strukov, D. B. & Stewart, D. R. Memristive devices     for computing. Nat. Nanotechnol.8, 13-24 (2013). -   [6]. Waser, R., Dittmann, R., Staikov, G. & Szot, K. Redox-based     resistive switching memories—Nanoionic mechanisms, prospects, and     challenges. Adv. Mater.21, 2632-2663 (2009). -   [7]. Pershin, Y. V. & Di Ventra, M. Memory effects in complex     materials and nanoscale systems. Adv. Phys. 60, 145-227 (2011). -   [8]. Wong, H. S. P., et al. Metal-oxide RRAM. Proc. IEEE 100,     1951-1970 (2012). -   [9]. Andy, T. Memristor-based neural networks. J. Phys. D: Appl.     Phys. 46, 093001 (2013). -   [10]. Giacomo, I. et al. Integration of nanoscale memristor synapses     in neuromorphic computing architectures. Nanotechnology 24, 384010     (2013). -   [11]. Jo, S. H. et al. Nanoscale memristor device as synapse in     neuromorphic systems. Nano Lett.10, 1297-1301 (2010). -   [12]. Kim, S. et al. Pattern recognition using carbon nanotube     synaptic transistors with an adjustable weight update protocol. ACS     Nano 11, 2814-2822 (2017). -   [13]. Kim, S. et al. Experimental demonstration of a second-order     memristor and its ability to biorealistically implement synaptic     plasticity. Nano Lett. 15, 2203-2211 (2015). -   [14]. Widrow, B. An adaptive adaline neuron using chemical     memistors. Stanford Electronics Laboratories Technical Report 1553-2     (1960). -   [15]. Lai, Q. et al. Ionic/electronic hybrid materials integrated in     a synaptic transistor with signal processing and learning functions.     Adv. Mater. 22, 2448-2453 (2010). -   [16]. Diorio, C., Hasler, P., Minch, A. & Mead, C. A. A     single-transistor silicon synapse. IEEE Trans. Electron Dev. 43,     1972-1980 (1996). -   [17]. Mouttet, B. Memristive systems analysis of 3-terminal devices.     IEEE Inter. Conf. Electron., Circuits & Systems 930-933 (2010). -   [18]. Azizi, A. et al. Dislocation motion and grain boundary     migration in two-dimensional tungsten disulphide. Nat. Commun. 5,     4867 (2014). -   [19]. Komsa, H.-P. et al. From point to extended defects in     two-dimensional MoS₂: Evolution of atomic structure under electron     irradiation. Phys. Rev. B 88, 035301 (2013). -   [20]. Sangwan, V. K. et al. Gate-tunable memristive phenomena     mediated by grain boundaries in single-layer MoS₂ . Nat.     Nanotechnol. 10, 403-406 (2015). -   [21]. Yu, Z. G., Zhang, Y.-W. & Yakobson, B. I. An anomalous     formation pathway for dislocation-sulfur vacancy complexes in     polycrystalline monolayer MoS₂ . Nano Lett. 15, 6855-6861 (2015). -   [22]. Bessonov, A. A. et al. Layered memristive and memcapacitive     switches for printable electronics. Nat. Mater. 14, 199-204 (2015). -   [23]. He, G. et al. Thermally assisted nonvolatile memory in     monolayer MoS₂ transistors. Nano Lett. 16, 6445-6451 (2016). -   [24]. Arnold, A. J. et al. Mimicking neurotransmitter release in     chemical synapses via hysteresis engineering in MoS₂ transistors.     ACS Nano 11, 3110-3118 (2017). -   [25]. Chua, L. Resistance switching memories are memristors. Appl.     Phys. A102, 765-783 (2011). -   [26]. Shannon, J. M. Control of Schottky barrier height using highly     doped surface layers. Sol. Stat. Electron. 19, 537-543 (1976). -   [27]. Sze, S. M. & Ng, K. K. Physics of Semiconductor Devices.     Wiley-Interscience, 2006. -   [28]. Prodromakis, T., Peh, B. P., Papavassiliou, C. & Toumazou, C.     A versatile memristor model with nonlinear dopant kinetics. IEEE     Trans. Electron Dev. 58, 3099-3105 (2011). -   [29]. Lembke, D. & Kis, A. Breakdown of high-performance monolayer     MoS₂ transistors. ACS Nano 6, 10070-10075 (2012). -   [30]. Yang, Y., Chen, B. & Lu, W. D. Memristive physically evolving     networks enabling the emulation of heterosynaptic plasticity. Adv.     Mater. 27, 7720-7727 (2015). -   [31]. Wang, I. T. et al. 3D Ta/TaO_(x)/TiO₂/Ti synaptic array and     linearity tuning of weight update for hardware neural network     applications. Nanotechnology 27, 365204 (2016). -   [32]. Bi, G.-Q. & Poo, M.-M. Synaptic modifications in cultured     hippocampal neurons: Dependence on spike timing, synaptic strength,     and postsynaptic cell type. J. Neurosci. 18, 10464-10472 (1998). -   [33]. Shastry, T. A. et al. Mutual photoluminescence quenching and     photovoltaic effect in large-area single-layer MoS₂-polymer     heterojunctions. ACS Nano 10, 10573-10579 (2016). -   [34]. Liu, X. et al. Rotationally commensurate growth of MoS₂ on     epitaxial graphene. ACS Nano 10, 1067-1075 (2016). -   [35]. Lee, C. et al. Anomalous lattice vibrations of single- and     few-layer MoS₂. ACS Nano 4, 2695-2700 (2010). -   [36]. Kim, I. S. et al. Influence of stoichiometry on the optical     and electrical properties of chemical vapor deposition derived MoS₂     . ACS Nano 8, 10551-10558 (2014). -   [37]. Sze, S. M. & Ng, K. K. Physics of Semiconductor Devices.     Wiley-Interscience, 2006. -   [38]. Chen, J.-R. et al. Control of Schottky barriers in single     layer MoS₂ transistors with ferromagnetic contacts. Nano Lett. 13,     3106-3110 (2013). -   [39]. Chua, L. Memristor-the missing circuit element. IEEE     Transactions on Circuit Theory 18, 507-519 (1971). -   [40]. Chua, L. Resistance switching memories are memristors. Appl.     Phys. A 102, 765-783 (2011). -   [41]. Chua, L.O. & Sung Mo, K. Memristive devices and systems. Proc.     IEEE 64, 209-223 (1976). -   [42]. Strukov, D. B., Snider, G. S., Stewart, D. R. &     Williams, R. S. The missing memristor found. Nature 453, 80-83     (2008). -   [43]. Mouttet, B. Memristive systems analysis of 3-terminal devices.     IEEE Inter. Conf. Electron., Circuits & Systems 930-933 (2010). -   [44]. Shannon, J. M. Control of Schottky barrier height using highly     doped surface layers. Sol. Stat. Electron. 19, 537-543 (1976). -   [45]. Shannon, J. M. Reducing the effective height of a Schottky     barrier using low-energy ion implantation. Appl. Phys. Lett. 24,     369-371 (1974). -   [46]. Shannon, J. M. Increasing the effective height of a Schottky     barrier using low-energy ion implantation. Appl. Phys. Lett. 25,     75-77 (1974). -   [47]. Kedzierski, J., et al. Complementary silicide source/drain     thin-body MOSFETs for the 20 nm gate length regime. International     Electron Devices Meeting 2000. Technical Digest. IEDM (Cat.     No.00CH37138) 57-60 (2000). -   [48]. Calvet, L. E. Electrical transport in Schottky barrier     MOSFETs. PhD thesis, Yale, 2001. -   [49]. Diorio, C., Hasler, P., Minch, A. & Mead, C. A. A     single-transistor silicon synapse. IEEE Trans. Electron Dev. 43,     1972-1980 (1996). -   [50]. Lai, Q. et al. Ionic/electronic hybrid materials integrated in     a synaptic transistor with signal processing and learning functions.     Adv. Mater. 22, 2448-2453 (2010). -   [51]. Sawa, A. Resistive switching in transition metal oxides.     Mater. Today 11, 28-36 (2008). -   [52]. Kubicek, M., Schmitt, R., Messerschmitt, F. & Rupp, J. L. M.     Uncovering two competing switching mechanisms for epitaxial and     ultrathin strontium titanate-based resistive switching bits. ACS     Nano9, 10737-10748 (2015). -   [53]. Lee, H.-S. et al. Ferroelectric tunnel junction for dense     cross-point arrays. ACS Appl. Mater. Interfaces 7, 22348-22354     (2015). -   [54]. Kim, D. J. et al. Ferroelectric tunnel memristor. Nano Lett.     12, 5697-5702 (2012). -   [55]. Nakamura, M. et al. Interface band profiles of     Mott-insulator/Nb:SrTiO₃ heterojunctions as investigated by optical     spectroscopy. Phys. Rev. B 82, 201101 (2010). -   [56]. Sawa, A., Fujii, T., Kawasaki, M. & Tokura, Y. Hysteretic     current-voltage characteristics and resistance switching at a     rectifying Ti/Pr_(0.7)Ca_(0.3)MnO₃ interface. Appl. Phys. Lett. 85,     4073-4075 (2004). -   [57]. Yang, J. J., Strukov, D. B. & Stewart, D. R. Memristive     devices for computing. Nat. Nanotechnol. 8, 13-24 (2013). -   [58]. Streetman, B. G. & Banerjee, S. K. Solid State Electronic     Devices. Prentice Hall, 2005. -   [59]. Prodromakis, T., Peh, B. P., Papavassiliou, C. & Toumazou, C.     A versatile memristor model with nonlinear dopant kinetics. IEEE     Trans. Electron Dev. 58, 3099-3105 (2011). -   [60]. Liu, W. et al. Impact of contact on the operation and     performance of back-gated monolayer MoS₂ field-effect-transistors.     ACS Nano 9, 7904-7912 (2015). -   [61]. Dankert, A., Langouche, L., Kamalakar, M. V. & Dash, S. P.     High-performance molybdenum disulfide field-effect transistors with     spin tunnel contacts. ACS Nano 8, 476-482 (2014). -   [62]. Lee, S., Tang, A., Aloni, S. & Wong, H. S. P. Statistical     study on the Schottky barrier reduction of tunneling contacts to CVD     synthesized MoS₂ . Nano Lett. 16, 276-281 (2016). -   [63]. Wang, J. et al. High mobility MoS₂ transistor with low     Schottky barrier contact by using atomic thick h-BN as a tunneling     layer. Adv. Mater. 28, 8302-8308 (2016). 

What is claimed is:
 1. A memtransistor, comprising: a substrate having a first surface and an opposite, second surface; a polycrystalline monolayer film formed of an atomically thin material on the first surface of the substrate, wherein the polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof; an electrode array having a plurality of electrodes spatial-apart formed on the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween; and a gate electrode formed on the second surface of the substrate and capacitively coupled with the channel.
 2. The memtransistor of claim 1, wherein the grains have an average grain size of about 1-10 μm.
 3. The memtransistor of claim 1, wherein the memtransistor is configured such that the Schottky barrier localized at each electrode is dynamically tunable so as to cause switching from a high resistance state (HRS) to a low resistance state (LRS) or from the LRS to the HRS in the memtransistor.
 4. The memtransistor of claim 3, wherein the memtransistor combines resistive switching with transistor gating to realize nonlinear charge transport with wide tunability of individual states and switching ratios.
 5. The memtransistor of claim 4, wherein a switching mechanism of the memtransistor is characterizable with two memristors at the contacts connected by a field-effect transistor.
 6. The memtransistor of claim 3, wherein the grain boundaries in the polycrystalline monolayer film enable the memtransistor to have large switching ratios and prevent electrical breakdown by lowering the Schottky barriers through dynamic defect migration, and control devices on single grains of the polycrystalline monolayer film show a qualitatively different reversible breakdown phenomenon.
 7. The memtransistor of claim 1, wherein the memtransistor is fabricated in a field-effect geometry with channel lengths (L) and widths (W), each varying from 1 μm to 250 μm.
 8. The memtransistor of claim 7, wherein L=1-15 μm, and W=100-150 μm.
 9. The memtransistor of claim 1, wherein the atomically thin material comprises MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials.
 10. The memtransistor of claim 1, wherein the substrate is formed of oxidized silicon (SiO₂), or dielectrics including alumina, hafnia, or zirconia.
 11. The memtransistor of claim 1, wherein the gate electrode is formed of highly doped silicon (Si), or other conductive materials.
 12. The memtransistor of claim 1, wherein each electrode of the electrode array is formed of a same metallic material or different metallic materials.
 13. The memtransistor of claim 5, wherein the electrode array is formed of at least one of gold (Au), titanium (Ti), and other conductive materials.
 14. The memtransistor of claim 1, being an LRS-HRS memtransistor or an LRS-LRS memtransistor.
 15. A circuitry, comprising one or more memtransistors according to claim
 1. 16. An electronic device, comprising one or more memtransistors according to claim
 1. 17. A memtransistor, comprising: a polycrystalline monolayer film formed of an atomically thin material, wherein the polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof; and an electrode array formed on the polycrystalline monolayer film, wherein the electrode array has a plurality of electrodes electrically coupled with the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween.
 18. The memtransistor of claim 17, wherein the grains have an average grain size of about 1-10 μm.
 19. The memtransistor of claim 17, wherein the memtransistor is configured such that the Schottky barrier localized at each electrode is dynamically tunable so as to cause switching from a high resistance state (HRS) to a low resistance state (LRS) or from the LRS to the HRS in the memtransistor.
 20. The memtransistor of claim 19, wherein the memtransistor combines resistive switching with transistor gating to realize nonlinear charge transport with wide tunability of individual states and switching ratios.
 21. The memtransistor of claim 20, wherein a switching mechanism of the memtransistor is characterizable with two memristors at the contacts connected by a field-effect transistor.
 22. The memtransistor of claim 19, wherein the grain boundaries in the polycrystalline monolayer film enable the memtransistor to have large switching ratios and prevent electrical breakdown by lowering the Schottky barriers through dynamic defect migration, and control devices on single grains of the polycrystalline monolayer film show a qualitatively different reversible breakdown phenomenon.
 23. The memtransistor of claim 17, wherein the atomically thin material comprises MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials.
 24. The memtransistor of claim 17, wherein each electrode of the electrode array is formed of a same metallic material or different metallic materials.
 25. The memtransistor of claim 24, wherein the electrode array is formed of at least one of gold (Au), titanium (Ti), and other conductive materials.
 26. The memtransistor of claim 17, further comprising a gate electrode capacitively coupled with the channel.
 27. The memtransistor of claim 26, wherein the gate electrode is formed of highly doped silicon (Si), or other conductive materials.
 28. The memtransistor of claim 26, further comprising a dielectric layer formed between the polycrystalline monolayer film and the gate electrode.
 29. The memtransistor of claim 28, wherein the dielectric layer is formed of oxidized silicon (SiO₂) or dielectrics including alumina, hafnia, or zirconia.
 30. The memtransistor of claim 17, being an LRS-HRS memtransistor or an LRS-LRS memtransistor.
 31. A circuitry, comprising one or more memtransistors according to claim
 17. 32. An electronic device, comprising one or more memtransistors according to claim
 17. 33. A method for fabricating a memtransistor, comprising: growing a polycrystalline monolayer film on a substrate, wherein the polycrystalline monolayer film contains grains defining a plurality of grain boundaries thereof; and forming an electrode array on the grown polycrystalline monolayer film, wherein the electrode array has a plurality of electrodes electrically coupled with the polycrystalline monolayer film such that each pair of electrodes defines a channel in the polycrystalline monolayer film therebetween.
 34. The method of claim 33, wherein the polycrystalline monolayer film is grown by chemical vapor deposition (CVD) on the substrates.
 35. The method of claim 33, further comprising, prior to forming the electrode array on the grown polycrystalline monolayer film: coating a film of photoresist on the polycrystalline monolayer film to form a first structure; baking the first structure; exposing the first structure to UV light and developing the exposed first structure to form a second structure; patterning the second structure with a resist mask by reactive ion etching to form a third structure; and submerging the third structure in an N-Methyl-2-pyrrolidone (NMP) bath to remove the resist mask to form a patterned polycrystalline monolayer strips.
 36. The method of claim 35, wherein the electrode array is formed by patterning a negative photoresist, followed by thermal evaporation of metals and lift-off in NMP.
 37. The method of claim 35, wherein the memtransistor is an LRS-LRS memtransistors.
 38. The method of claim 35, further comprising, prior to coating the film of photoresist on the polycrystalline monolayer film: coating a film of polymethylglutarimide (PMGI) on the polycrystalline monolayer film; and baking the coated film of polymethylglutarimide (PMGI) on the polycrystalline monolayer film at about 170° C. for a period of time.
 39. The method of claim 38, wherein the memtransistor is an LRS-HRS memtransistor.
 40. The method of claim 33, wherein the polycrystalline monolayer film comprises an atomically thin material of MoS₂, MoSe₂, WS₂, WSe₂, or related two-dimensional materials.
 41. The method of claim 33, wherein the substrate is formed of oxidized silicon (SiO₂), or dielectrics including alumina, hafnia, or zirconia.
 42. The method of claim 33, further comprising forming a gate electrode on the substrate such that the substrate is positioned between the gate electrode and the polycrystalline monolayer film, wherein the gate electrode is capacitively coupled with the channel.
 43. The method of claim 42, wherein the gate electrode is formed of highly doped silicon (Si), or other conductive materials. 